201228689 六、發明說明： 【發明所屬之技術領域】 本發明係關於—種合金及其製造方法，特別是一種高 爾夫球桿頭合金及其製造方法。 【先前技術】 一般而s，為了符合不同使用者的需求，通常高爾夫 球桿頭-體成型之套頸需要具有易於調整傾角之特性，以 冑合使用者之需求。因此H高爾夫球桿頭通常係以低 硬度之軟鐵類材質製成，例如以低碳鋼或低合金鋼等材質 製成，使得高爾夫球桿頭之套頸具有前述易於調整傾角之 特性。然而，該些軟鐵類材質卻具有易於氧化而不耐鏽蝕 之缺點。 為改良上述缺點，中華民國公告第438610及460306 號皆有揭示以以SUS17-4PH規格之不鏽鋼材質製成該高 爾夫球桿頭，使得所製成之高爾夫球桿頭可同時具有低硬 φ 度及較佳之耐鏽蝕性。 該SUS17-4PH之機械性質及熱處理值分別如表一及 表二所示。 表一、SUS17-4PH之機械性質（棒材理論值) 材質名稱 抗拉強度 (Ksi) 降伏強度 (Ksi) 伸長量 (% in 2 Inches) 硬度 (HRC) SUS17-4PH 164 148 17 36 表二、SUS17-4PH之熱處理值 材質名稱 抗拉強度 (Ksi) 降伏強度 (Ksi) 伸長量 (% in 2 inches) 硬度 (HRC) 註 201228689 SUS17-4PH (鑄造） 145-160 145〜155 7〜14 32 〜37 A 160 〜170 180〜195 150〜165 6〜13 33 〜39 B 160〜180 5〜11 38-44 C SUS17-4PH (板材） 185-210 170〜190 5〜17 40-46 D 其中’表二中之註A的鑄造熱處理係指：固溶處理 1040°C均溫60分鐘氮氣冷卻，時效處理58〇〇C持溫90分 鐘；註B的鑄造熱處理係指：固溶處理1〇4〇°c均溫60分 鐘氮氣冷卻，時效處理538°C持溫240分鐘；註C的鑄造 熱處理係指：固溶處理l〇4〇°c均溫60分鐘氮氣冷卻，時 效處理482°C持溫240分鐘；註D的板材一般熱處理係指： 固溶處理1040。(：均溫60分鐘氮氣冷卻，時效處理482。(：持 溫240分鐘。 由表一及表二可得知，由於該SUS17-4PH不鏽鋼中， 鎳成分所佔比例僅約4.0wt%，因此延性較差，且仍然具有 較高之降伏強度值。若以該SUS17-4PH不鏽鋼作為高爾夫 球桿頭之材質，則該高爾夫球桿頭可能因延性較差或降伏 強度較高而造成調角不易之缺點。 基於上述原因，其有必要進一步改良上述習用高爾夫 球桿頭合金及其製作方法。 【發明内容】 本發明目的乃改良上述缺點，以提供一種高爾夫球桿 頭合金’透過調整銅/鎳比，以降低高爾夫球桿頭合金之硬 度、抗拉強度及降伏強度為目的。 本發明次一目的係提供一種高爾夫球桿頭合金，以使 該合金同時具有沃斯田鐵相、肥粒鐵相及麻田散鐵相之組 織0 201228689 本發明次一目的係提供一種高爾夫球桿頭合金之製 作方法，以將具有特定銅/鎳比之配比製作為同時具有沃斯 田鐵、肥粒鐵及麻田散鐵組織之合金。 根據本發明的高爾夫球桿頭合金’係包含：以重量百 分比計2.5〜4.0%之銅、5.0〜6.0%之鎳及15〜18%之鉻，殘 餘部分為鐵及不可避免之雜質所構成，其中，銅/鎳比係為 0.4〜0.8，且該合金同時具有沃斯田鐵相、肥粒鐵相及麻田 散鐵相之組織。 根據本發明的高爾夫球桿頭合金之製造方法，係包含 .一溶融步驟’依序將母合金、珍鐵、猛鐵、絡鐵、翻鐵 、銅及鎳加入高溫熔爐中，使該些金屬炫融混合；一比例 維持步驟，使該些炫融後之混合金屬包含有以重量百分比 計2.5〜4.0%之銅、5.0〜6.0%之錄及15〜18%之鉻，且銅/鎳 比係為0.4〜0.8 ’殘餘部分為鐵及不可避免之雜質所構成， 並維持該比例，使該熔融混合金屬可形成兼具有沃斯田鐵 相、肥粒鐵相及麻田散鐵相之合金；及一桿頭鑄造步驟， 將該合金進行精密鑄造以形成一高爾夫球桿頭。 【實施方式】 為讓本發明之上述及其他目的、特徵及優點能更明顯 易f董，下文特舉本發明之較佳實施例，並配合所附圖式， 作詳細說明如下： 印參照第1圖所示’本發明之高爾夫球桿頭合金之製 造方法主錢包含-純步驟S卜 一比例維持步驟S2及 /桿頭鑄造步驟S3。 201228689 請參照第1圖所示，本發明之炫融步驟sl係依序將 母合金、鉻鐵、銅及鎳等配料加入高溫嫁爐中，使該些配 料溶融混合。更詳言之’前述該些以鋼、絡、錄及鐵為主 要成分之配料受高溫溶爐〔例如高週波爐〕溶融後，便混 合形成具有特定組成比例及特定組成相之銅、鎳、鉻及鐵 等元素之合金材質’以供後續做為高岐球桿頭之基材 〔matrix〕。Λ中’本實施例所使用之母合金除鐵以外係 包含以重量百分輯讀％之碳、G.8G%^、丨_之摄、 6.38%之鎳、22.9%之鉻、請％之翻、G魏之構及〇桃 之硫。當然’亦可依據需求變換成不同配料來源，而溶融 形成具有相同組成比例之鐵合金材質。 此外，本發明較佳係依特定熔融順序將母合金、石夕 鐵、_、絡鐵、錮鐵、鋼、錄等配料加入高溫熔爐〔例 如高週波爐〕中進行合金炼煉製程，使得該溶融合金中另 is夕猛及銦等其他成分，進而使得炫煉出來之合金可 具有適當之特性。再且，依特定熔融順序加入該些配料可 以避免在畴_時發生沈觀象及防讀續製成之桿頭 成品良率減之_。再且，本實施例較健㈣呈現細 粒f:，之前述配料，並盡可能以少量多奴方式緩慢加入 該二皿熔爐巾，以避免因大量加人該配料，造成該配料無 法完全熔融而點結成團塊狀，進而造成使得高溫炼爐内部 產生空穴或氣泡而產生危險性。 、请再參照第1圖所示，本發明之比例維持步驟S2係 使前述該些配料之重量百分比維持在：25〜娜之銅、 5.0〜6.0%之錄、15〜18%之絡，殘餘部分為鐵及不可避免之 201228689 雜質’且使該銅/鎳比係為〇·4〜〇 8，以使該些配料可共同 形成同時兼具有沃斯田鐵相、肥粒鐵相及麻田散鐵相之組 織。更詳言之，當前述配料依序加入高溫熔爐以形成熔融 合金後，接著則取樣測量熔融合金之重量組成比例，以確 保該配料之重量百分比維持在：2 5〜4 〇0/〇之銅、5 〇〜6.〇〇/0 之鎳及15〜18%之鉻’殘餘部分為鐵（65〜75%)及不可避 免之雜質’且使該銅/鎳比為〇 4〜〇 8。該熔融合金中銅的 組成比例更佳係為2.8〜3.5% (以重量百分比計），鉻的更 佳比例係為15.5〜17% (以重量百分比計）。透過使該熔融 合金維持於該特定之組成比例及銅/鎳比，使得該熔融合金 冷卻固化後此形成兼具沃斯田鐵相〔austenite〕、肥粒鐵 相〔ferrite〕及麻田散鐵相之合金材質。其中，本案透過提 高該鎳之比例，以提升整體合金之延性；再且，若該熔融 合金中之銅/鎳比低於〇·4，則銅之比例相對較低，錄之比 例相對較高，冷卻固化後所形成之合金的強度可能不足； 若該熔融合金中之銅/鎳比高於〇 8，則銅之比例相對較 高，鎳之比例相對較低，冷卻固化後所形成之合金的硬度 可能過高’ Μ利於作為高爾夫球桿頭後續進行調角之動 作。因此，本案另透過使該銅/鎳比介於0.4〜〇·8，使得該 合金可同時具有低硬度及適t之強度。其中，該合金中^ 另包含其他金屬成分或部分雜質，例如其他金屬成分以重 量百分比計為0.65〜0.81%之矽、〇·66〜0.78%之錳戋 0.0〇2〜0.125%之翻，雜質如竣(c)、硫⑼或者卿)等成分， 以重量百分比計碳較佳係低於⑽6%，硫較佳係低於 0.019%，磷較佳係低於〇 〇27%。 _、 201228689 如前所述，本發明係藉由預定組成比例之鐵等各種元 素以及特定之銅/鎳比構成兼具沃斯田鐵相、肥粒鐵相及麻 田散鐵相之合金材質，使製成之合金材質能兼具肥粒鐵 相、沃斯田鐵相及麻田散鐵相之優點〔例如肥粒鐵相之耐 孔蝕性及低硬度，沃斯田鐵相之耐均勻鏽蝕性及耐衝擊 性，以及麻田散鐵相之咼耐磨性〕，並同時降低該三種鐵 相之缺點〔例如肥粒鐵相之低韌性及易發生^相脆化問 題，沃斯田鐵相之易發生孔蝕問題，以及麻田散鐵相之耐 蝕性不佳問題〕。如此，使本發明之高爾夫球桿頭合金可 具有適當之低硬度、尚延性等良好的機械性質。 請再參照第1圖所示，本發明之桿頭鑄造步驟S3係 以該合金進行精密鑄造，以形成預定形狀之高爾夫桿頭。 更詳言之，待確認該熔融合金符合前述預定之配比及銅/ 鎳比後，在出爐前進行除氣及除渣後，即可將其直接澆注 進入用以精密鑄造之-模具内，供製造預定形狀之高爾夫 球桿頭〔及/或其擊球面板〕，如此完錢鑄之高爾夫球桿 頭不需經由熱處理，即可進行震殼、去澆口、切邊、研磨、 =角、磨光等步驟以製錢桿或木桿之桿頭成品，且製得 才干頭之材質將兼具沃斯賴相、肥粒鐵相及麻田散鐵相之 混合組成相’㈣具㈣當域硬度、高耐祕性及高延 展性等特性。尤其該低硬度及高延性之特性將使桿頭在鑄 造時具有較佳流動性及成型性，以減少產生渣孔及氣孔； 再且，該低硬度之特性將使桿頭具有較大之可塑性，而易 於進行調角。 其中，該高爾夫球桿頭於鑄造完成後，若進一步與— 201228689 擊球面板進行焊接時，係於焊接後選擇以高溫回火處理， 以去除焊接產生之應力。 综上所述，透過前述之製程，便可獲得本案之高爾夫 球桿頭用之合金，該合金主要係包含以重量百分比計 15〜18%之鉻、2.5〜4.0%之銅及5.0〜6.0%之鎳，殘餘部分為 鐵及不可避免之雜質所構成，其中，銅/鎳比係為〇.4〜〇 8， 且該合金同時具有沃斯田鐵相、肥粒鐵相及麻田散鐵相之 組織。藉此，以使該高爾夫球桿頭用之合金具有低硬度、 高延性及高耐蝕性，有利於高爾夫球桿頭之調角。其中， 該合金較佳係另包含〇·65〜0.81%之矽、0.66〜0.78%之鐘及 0.002〜0.125%之鉬，以適當調整該合金之特性。 請參照表一至表三所示，表一係為本案與習用 SUS17-4PH不鏽鋼之組成差異表。表二係為本發明之高爾 夫球桿頭用之合金的各種不同實施例之成分表。表三係為 本發明各種不同實施例之機械性質表。 由結果可明顯得知，本案透過提高鎳之組成，並同時 控制銅/鎳比介於0.4〜〇.8之間，可以降低合金之硬度，並 可降低該合金之降伏強度，有利於高爾夫球桿頭之調角。 表、本發明及習用高爾夫球桿頭合金之組成比例之 對照表〔單位為wt%〕。 規 格 銅Cu 鎳NI 鉻Cr 鐵Fe 銅/鎳比 SUS17-4PH 3.0-5.0 3.0-5.0 15.5-17.5 Bal. 本發明合金 2.5-4 5〜6 15 〜18 Bal. 0.4-Ό.8 表二、本發明及習用高爾夫球桿頭合金之物理性質之 對照表。 ' 201228689 本案合 金之實 施例 組成成分(％) C Si Μη S P Cu Ni Cr Mo Fe Cu/Ni 1 0.043 0.711 0.765 0.012 0.024 2.543 5.014 15.145 0.115 Bal. 0.5 2 0.045 0.685 0.701 0.011 0.019 3.321 5.095 15.025 0.114 Bal. 0.66 3 0.048 0.695 0.745 0.009 0.014 3.985 5.041 15.085 0.115 Bal. 0.8 4 0.051 0.674 0.698 0.014 0.025 2.587 5.102 16.574 0.118 Bal. 0.5 5 0.054 0.701 0.685 0.013 0.025 3.356 5.016 16.599 0.119 Bal. 0.66 6 0.053 0.724 0.699 0.018 0.018 4.014 5.095 16.471 0.114 Bal. 0.8 7 0.058 0.801 0.752 0.017 0.021 2.544 5.041 18.147 0.114 Bal. 0.5 8 0.049 0.758 0.774 0.019 0.023 3.366 5.145 18.096 0.116 Bal. 0.66 9 0.048 0.774 0.698 0.019 0.018 4.095 4.954 18.065 0.125 Bal. 0.8 10 0.048 0.722 0.701 0.019 0.026 2.601 5.474 15.145 0.114 Bal. 0.45 11 0.051 0.658 0.725 0.015 0.027 3.385 5.568 15.021 0.002 Bal. 0.6 12 0.052 0.699 0.766 0.018 0.022 4.085 5.574 15.036 0.113 Bal. 0.73 13 0.049 0.701 0.698 0.014 0.023 2.536 5.569 16.587 0.112 Bal. 0.45 14 0.056 0.715 0.668 0.014 0.023 3.398 5.601 16.471 0.009 Bal. 0.6 15 0.049 0.724 0.714 0.015 0.021 4.012 5.478 16.645 0.111 Bal. 0.73 16 0.053 0.714 0.722 0.016 0.024 2.563 5.501 18.156 0.117 Bal. 0.45 17 0.058 0.733 0.725 0.016 0.025 3.285 5.520 18.245 0.114 Bal. 0.6 18 0.054 0.723 0.735 0.015 0.021 4.098 5.529 18.104 0.119 Bal. 0.73 19 0.055 0.698 0.741 0.011 0.022 2.514 6.098 15.098 0.112 Bal. 0.42 20 0.052 0.688 0.699 0.012 0.021 3.298 6.105 14.895 0.113 Bal. 0.55 21 0.051 0.674 0.701 0.011 0.023 4.074 5.965 15.147 0.009 Bal. 0.67 22 0.051 0.742 0.735 0.017 0.020 2.589 5.987 16.589 0.118 Bal. 0.42 23 0.055 0.713 0.744 0.014 0.019 3.313 6.023 16.643 0.119 Bal. 0.55 24 0.048 0.725 0.724 0.016 0.021 4.145 6.097 16.412 0.111 Bal. 0.67 25 0.050 0.696 0.710 0.015 0.024 2.451 6.012 18.013 0.115 Bal. 0.42 26 0.048 0.699 0.706 0.016 0.023 3.325 5.967 18.098 0.116 Bal. 0.55 27 0.049 0.703 0.698 0.019 0.022 4.085 6.087 17.945 0.114 Bal. 0.67 表三、本發明及習用高爾夫球桿頭合金之機械性質之 對照表。 本案合金 之實施例 抗拉強度(ksi) 降伏強度(ksi) 伸長量(％) 硬度(HRC) Cu/Ni 值 1 159.4 87.3 13.2 32.5 0.5 2 161.0 89.1 11.3 33.5 0.66 3 163.3 90.2 10.4 34.1 0.8 —10 — 201228689 4 154.7 85.4 14.2 30.7 0.5 5 156.8 86.2 13.9 31.0 0.66 6 157.6 86.3 13.8 31.2 0.8 7 152.3 83.5 14.8 29.8 0.5 8 152.9 85.4 14.5 30.1 0.66 9 154.9 85.9 14.1 30.6 0.8 10 152.2 79.8 17.1 ~~ 26.5 0.45 11 154.1 79.9 16.9 26.7 0.6 12 153.2 80.1 16.8 26.5 0.73 13 149.2 77.1 18.6 25.1 0.45 14 149.8 78.6 17.9 26.3 0.6 15 151.2 79.8 16.4 26.9 0.73 16 138.7 68.9 19.2 22.1 0.45 17 139.6 69.3 18.6 23.3 0.6 18 139.5 68.4 18.8 22.9 0.73 19 138.4 67.2 20.1 20.8 0.42 20 139.6 69.4 19.4 22.1 0.55 21 142.1 70.1 19.2 21.9 0.67 22 131.2 62.1 20.3 20.2 0.42 23 132.4 63.1 19.9 20.9 0.55 24 135.1 66.1 19.1 21.3 0.67 25 126.4 59.6 22.4 19.4 0.42 26 129.1 59.8 21.7 19.9 0.55 27 132.5 62.1 20.1 20.5 0.67 請再參照第2及3圖，其係將本發明之高爾夫球桿頭 合金於鑄造後，以 10g K3Fe(CN)6 + l〇g KOH + 100ml H20 之腐蝕液進行腐蝕後之合金材料的金相組織圖。該第1及 2圖分別為本發明之合金200倍及500倍放大之顯微組織 圖，由圖可得知其為包含肥粒鐵、奥斯田鐵及麻田散鐵三 相共存之Fe-Cr-Ni合金，亦即同時擁有三相之強度及延性 等特點。可驗證本案之合金透過適當控制鋼/錄比，確實可 使該合金同時具有肥粒鐵、奥斯田鐵及麻田散鐵三相共存 之結構。 ^ ’’示上所述，本發明高爾夫球桿頭合金係以特定比例之 201228689 銅/鎳比製作該合金，以降低該合金之硬度、抗拉強度及降 伏強度’使得該合錢於製作高爾夫球桿頭具有易於調角 之優點。 '11 本發明高爾夫球桿頭合金係以特定比例之鋼/鎳比製 作該合金，使得該合金同時具有沃斯田鐵相、肥粒鐵相及 麻田散鐵相之組織。 —本發明高爾夫球桿頭合金之製作方法係透過調整特 定之銅/錄比’用以製作出前述具有低硬度之三相不鐵鋼合 金。 雖然本發明已利用上述較佳實施例揭示，然其並非用 以限定本發明，任何熟習此技藝者在不脫離本發明之精神 和範圍之内，相對上述實施例進行各種更動與修改仍屬本 發明所保護之技術範_，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··本發明之高爾夫球桿頭合金之製造方法的流程鲁 圖。 第2圖：本發明之高爾夫球桿頭合金之金相組織圖（200 倍）。 第3圖：本發明之高爾夫球桿頭合金之金相組織圖（500 倍）。 【主要元件符號說明】201228689 VI. Description of the Invention: TECHNICAL FIELD OF THE INVENTION The present invention relates to an alloy and a method of manufacturing the same, and more particularly to a golf club head alloy and a method of manufacturing the same. [Prior Art] In general, in order to meet the needs of different users, the golf club head-body forming neck needs to have the characteristics of easy adjustment of the inclination angle to meet the needs of the user. Therefore, the H golf club head is usually made of a soft iron material of low hardness, for example, made of low carbon steel or low alloy steel, so that the neck of the golf club head has the aforementioned characteristics of easy adjustment of the inclination angle. However, these soft iron materials have the disadvantage of being easily oxidized and not resistant to rust. In order to improve the above-mentioned shortcomings, the Republic of China Bulletin Nos. 438610 and 460306 disclose that the golf club head is made of SUS17-4PH stainless steel, so that the golf club head can have a low hardness and Better rust resistance. The mechanical properties and heat treatment values of the SUS17-4PH are shown in Tables 1 and 2, respectively. Table 1. Mechanical properties of SUS17-4PH (theoretical value of bar) Material name Tensile strength (Ksi) Degradation strength (Ksi) Elongation (% in 2 Inches) Hardness (HRC) SUS17-4PH 164 148 17 36 Table 2 SUS17-4PH heat treatment value material name tensile strength (Ksi) drop strength (Ksi) elongation (% in 2 inches) hardness (HRC) Note 201228689 SUS17-4PH (casting) 145-160 145~155 7~14 32 ~ 37 A 160 ~ 170 180~195 150~165 6~13 33 ~ 39 B 160~180 5~11 38-44 C SUS17-4PH (plate) 185-210 170~190 5~17 40-46 D where 'table The casting heat treatment of Note A of the second part refers to: solution treatment at 1040 ° C for 60 minutes, nitrogen cooling, aging treatment at 58 ° C for 90 minutes; injection heat treatment of Note B means: solution treatment 1 〇 4 〇 °C average temperature 60 minutes nitrogen cooling, aging treatment 538 ° C holding temperature 240 minutes; injection C casting heat treatment refers to: solution treatment l〇4〇 ° c average temperature 60 minutes nitrogen cooling, aging treatment 482 ° C temperature 240 minutes; the general heat treatment of the sheet of Note D means: solution treatment 1040. (: Nitrogen cooling for 60 minutes at room temperature, aging treatment 482. (: Hold temperature for 240 minutes. As can be seen from Table 1 and Table 2, since the proportion of nickel component in the SUS17-4PH stainless steel is only about 4.0% by weight, The ductility is poor, and still has a high value of the relief strength. If the SUS17-4PH stainless steel is used as the material of the golf club head, the golf club head may have difficulty in adjusting the angle due to poor ductility or high drop strength. For the above reasons, it is necessary to further improve the above-described conventional golf club head alloy and a manufacturing method thereof. SUMMARY OF THE INVENTION The object of the present invention is to improve the above disadvantages to provide a golf club head alloy 'transmission adjustment copper/nickel ratio, The purpose of the invention is to reduce the hardness, tensile strength and strength of the golf club head alloy. The second object of the invention is to provide a golf club head alloy, so that the alloy has both a Wolster iron phase and a ferrite phase and The organization of the Matian iron phase 0 201228689 The second object of the present invention is to provide a method for manufacturing a golf club head alloy to have a specific copper/nickel ratio It is made of an alloy having both Worthite iron, ferrite iron and 麻田散铁 structure. The golf club head alloy according to the present invention comprises: 2.5 to 4.0% by weight of copper, 5.0 to 6.0% of nickel by weight. And 15~18% chromium, the residual part is composed of iron and unavoidable impurities, wherein the copper/nickel ratio is 0.4~0.8, and the alloy has both Worthfield iron phase, fat grain iron phase and Ma Tiansan The structure of the iron phase alloy according to the present invention includes a melting step of sequentially adding a master alloy, a rare iron, a razor iron, a complex iron, a turn iron, copper and nickel to a high temperature furnace. And mixing the metals; a ratio maintaining step, wherein the mixed metal after the blending comprises 2.5 to 4.0% by weight of copper, 5.0 to 6.0% of the recorded, and 15 to 18% of the chromium, And the copper/nickel ratio is 0.4 to 0.8'. The residual portion is composed of iron and unavoidable impurities, and the ratio is maintained, so that the molten mixed metal can form both the Worthfield iron phase, the fertilized iron phase, and the 麻田. An alloy of iron and iron; and a casting step of the head, the alloy The above-described and other objects, features and advantages of the present invention will become more apparent. The preferred embodiments of the invention are described below The drawings are described in detail as follows: The printing method of the golf club head alloy according to the present invention is shown in Fig. 1. The main method includes a pure step S and a ratio maintaining step S2 and/or a head casting step S3. Referring to Fig. 1, the step s1 of the present invention sequentially adds the parent alloy, ferrochrome, copper and nickel to the high temperature wedding furnace to melt and mix the ingredients. More specifically, the foregoing The ingredients containing steel, complex, recorded and iron as main components are melted in a high-temperature furnace (such as a high-frequency furnace), and then mixed to form an alloy material having elements of specific composition and specific composition of copper, nickel, chromium and iron. 'For subsequent use as the base of the sorghum club head [matrix]. In the case of the master alloy used in this example, except for iron, the carbon content, G.8G%^, 丨_, 6.38% nickel, 22.9% chromium, %% Turn over, the structure of G Wei and the sulfur of peach. Of course, it can be transformed into different sources of ingredients according to demand, and melted to form a ferroalloy material having the same composition ratio. In addition, the present invention preferably applies a master alloy, a stellite iron, a ruthenium, a ferroniobium, a ruthenium, a steel, a recording, and the like to a high-temperature furnace (for example, a high-frequency furnace) to perform an alloy refining process according to a specific melting sequence, so that the alloying process is performed. Other components such as indium and indium are dissolved in the fusion gold, which in turn allows the alloy to be sleek to have appropriate characteristics. Moreover, the addition of the ingredients in a particular order of melting avoids the occurrence of sinking in the domain and the reduction in the yield of the finished product. Moreover, the present embodiment is more robust (four) presenting the fine particles f:, the aforementioned ingredients, and slowly adding the two-smelting furnace towel as much as possible in a small amount of slaves to avoid the incomplete melting of the ingredients due to the large amount of the ingredients added. However, the dots are agglomerated, which causes a danger of generating voids or bubbles inside the high-temperature furnace. Referring to FIG. 1 again, the ratio maintaining step S2 of the present invention maintains the weight percentage of the above ingredients in: 25~Na, copper, 5.0~6.0%, 15~18%, residual Part of the iron and the inevitable 201228689 impurity' and the copper/nickel ratio is 〇·4~〇8, so that the ingredients can be formed together with both the Worthfield iron phase, the ferrite grain phase and the 麻田The organization of the scattered iron phase. More specifically, when the foregoing ingredients are sequentially added to the high-temperature furnace to form a molten alloy, then the weight composition ratio of the molten alloy is sampled to ensure that the weight percentage of the ingredients is maintained at: 2 5~4 〇0/〇 copper 5, 〇~6. 〇〇/0 of nickel and 15~18% of chromium 'residual part is iron (65~75%) and unavoidable impurities' and the copper/nickel ratio is 〇4~〇8. The composition ratio of copper in the molten alloy is more preferably 2.8 to 3.5% by weight, and a more preferable ratio of chromium is 15.5 to 17% by weight. By maintaining the molten alloy at the specific composition ratio and the copper/nickel ratio, the molten alloy is cooled and solidified to form both the austenite, the ferrite, and the granitic iron phase. Alloy material. Among them, the case improves the ductility of the overall alloy by increasing the proportion of the nickel; furthermore, if the copper/nickel ratio in the molten alloy is lower than 〇·4, the proportion of copper is relatively low, and the ratio is relatively high. The strength of the alloy formed after cooling and solidification may be insufficient; if the copper/nickel ratio in the molten alloy is higher than 〇8, the proportion of copper is relatively high, the proportion of nickel is relatively low, and the alloy formed after cooling and solidification The hardness may be too high' to facilitate the subsequent adjustment of the golf club head. Therefore, in the present case, by making the copper/nickel ratio between 0.4 and 〇·8, the alloy can have both low hardness and moderate strength. Wherein, the alloy further contains other metal components or partial impurities, for example, other metal components are 0.65~0.81% by weight, 〇·66~0.78% of manganese 戋0.0〇2~0.125%, impurities For components such as ruthenium (c), sulphur (9) or sulphur, the carbon is preferably less than (10) 6% by weight, the sulphur is preferably less than 0.019%, and the phosphorus is preferably less than 〇〇27%. _, 201228689 As described above, the present invention constitutes an alloy material of a Worthite iron phase, a ferrite grain iron phase, and a Matian bulk iron phase by various elements such as iron of a predetermined composition ratio and a specific copper/nickel ratio. The alloy material can be made to have both the ferrite phase, the Worthfield iron phase and the Matian iron phase (such as the pitting resistance and low hardness of the ferrite phase, and the uniform corrosion of the Worthfield iron phase) Sex and impact resistance, and the wear resistance of the ferrous phase of the granules, and at the same time reduce the shortcomings of the three iron phases (such as the low toughness of the ferrite grain iron phase and the easy occurrence of phase embrittlement problems, Worthfield iron phase It is prone to pitting corrosion problems and poor corrosion resistance of the Matian iron phase. Thus, the golf club head alloy of the present invention can have good mechanical properties such as low hardness and ductility. Referring again to Fig. 1, the head casting step S3 of the present invention is precision casted with the alloy to form a golf club head of a predetermined shape. More specifically, after confirming that the molten alloy meets the predetermined ratio and the copper/nickel ratio, after degassing and slag removal before tapping, it can be directly poured into a mold for precision casting. A golf club head (and/or its batting panel) for making a predetermined shape, so that the golf club head can be shaken, de-gated, trimmed, ground, or angled without heat treatment. , polishing and other steps to make the money rod or wood rod head finished, and the material made of the dry head will have a mixture of Voss Lai, fat grain iron phase and Ma Tian loose iron phase '(four) with (four) Domain hardness, high resistance to sedentity and high ductility. In particular, the low hardness and high ductility characteristics will make the head have better fluidity and formability during casting to reduce the generation of slag holes and pores. Moreover, the low hardness characteristic will make the head have greater plasticity. And easy to adjust the angle. Wherein, after the casting is completed, if the ball is further welded with the 201228689 ball striking panel, it is selected to be tempered at a high temperature after welding to remove the stress generated by the welding. In summary, through the foregoing process, the alloy for golf club head of the present invention can be obtained, which mainly comprises 15~18% chromium, 2.5~4.0% copper and 5.0~6.0% by weight percent. Nickel, the remainder is composed of iron and unavoidable impurities, wherein the copper/nickel ratio is 〇.4~〇8, and the alloy has both Worthfield iron phase, fat grain iron phase and 麻田散铁相Organization. Thereby, the alloy for the golf club head has low hardness, high ductility and high corrosion resistance, which is advantageous for the angle adjustment of the golf club head. Preferably, the alloy further comprises ruthenium 65 to 0.81%, 0.66 to 0.78% of the bell, and 0.002 to 0.125% of molybdenum to appropriately adjust the characteristics of the alloy. Please refer to Tables 1 to 3, Table 1 is the difference table between the case and the conventional SUS17-4PH stainless steel. Table 2 is a list of the compositions of various embodiments of the alloy for the golf club head of the present invention. Table 3 is a table of mechanical properties for various embodiments of the present invention. It can be clearly seen from the results that in this case, by increasing the composition of nickel and controlling the copper/nickel ratio between 0.4 and 〇.8, the hardness of the alloy can be lowered, and the lodging strength of the alloy can be lowered, which is advantageous for golf balls. The adjustment of the head. A comparison table (unit: wt%) of the composition ratio of the watch, the present invention and the conventional golf club head alloy. Specification Copper Cu Nickel NI Chromium Cr Iron Fe Copper/Nickel Ratio SUS17-4PH 3.0-5.0 3.0-5.0 15.5-17.5 Bal. Alloy of the Invention 2.5-4 5~6 15~18 Bal. 0.4-Ό.8 Table II. A comparison table of the physical properties of the inventive and conventional golf club head alloys. '201228689 Example composition of the alloy of the case (%) C Si Μη SP Cu Ni Cr Mo Fe Cu/Ni 1 0.043 0.711 0.765 0.012 0.024 2.543 5.014 15.145 0.115 Bal. 0.5 2 0.045 0.685 0.701 0.011 0.019 3.321 5.095 15.025 0.114 Bal. 0.66 3 0.048 0.695 0.745 0.009 0.014 3.985 5.041 15.085 0.115 Bal. 0.8 4 0.051 0.674 0.698 0.014 0.025 2.587 5.102 16.574 0.118 Bal. 0.5 5 0.054 0.701 0.685 0.013 0.025 3.356 5.016 16.599 0.119 Bal. 0.66 6 0.053 0.724 0.699 0.018 0.018 4.014 5.095 16.471 0.114 Bal 0.8 7 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0.114 Bal. 0.45 11 0.051 0.658 0.725 0.015 0.027 3.385 5.568 15.021 0.002 Bal. 0.6 12 0.052 0.699 0.766 0.018 0.022 4.085 5.574 15.036 0.113 Bal. 0.73 13 0.049 0.701 0.698 0.014 0.023 2.536 5.569 16.587 0.112 Bal. 0.45 14 0.056 0.715 0.668 0.01 4 0.023 3.398 5.601 16.471 0.009 Bal. 0.6 15 0.049 0.724 0.714 0.015 0.021 4.012 5.478 16.645 0.111 Bal. 0.73 16 0.053 0.714 0.722 0.016 0.024 2.563 5.501 18.156 0.117 Bal. 0.45 17 0.058 0.733 0.725 0.016 0.025 3.285 5.520 18.245 0.114 Bal. 0.6 18 0.054 0.723 0.735 0.015 0.021 4.098 5.529 18.104 0.119 Bal. 0.73 19 0.055 0.698 0.741 0.011 0.022 2.514 6.098 15.098 0.112 Bal. 0.42 20 0.052 0.688 0.699 0.012 0.021 3.298 6.105 14.895 0.113 Bal. 0.55 21 0.051 0.674 0.701 0.011 0.023 4.074 5.965 15.147 0.009 Bal. 0.67 22 0.051 0.742 0.735 0.017 0.020 2.589 5.987 16.589 0.118 Bal. 0.42 23 0.055 0.713 0.744 0.014 0.019 3.313 6.023 16.643 0.119 Bal. 0.55 24 0.048 0.725 0.724 0.016 0.021 4.145 6.097 16.412 0.111 Bal. 0.67 25 0.050 0.696 0.710 0.015 0.024 2.451 6.012 18.013 0.115 Bal 0.42 26 0.048 0.699 0.706 0.016 0.023 3.325 5.967 18.098 0.116 Bal. 0.55 27 0.049 0.703 0.698 0.019 0.022 4.085 6.087 17.945 0.114 Bal. 0.67 Table 3, the machine of the present invention and the conventional golf club head alloy The quality table. Examples of Alloys in this Case Tensile Strength (ksi) Degradation Strength (ksi) Elongation (%) Hardness (HRC) Cu/Ni Value 1 159.4 87.3 13.2 32.5 0.5 2 161.0 89.1 11.3 33.5 0.66 3 163.3 90.2 10.4 34.1 0.8 —10 — 201228689 4 154.7 85.4 14.2 30.7 0.5 5 156.8 86.2 13.9 31.0 0.66 6 157.6 86.3 13.8 31.2 0.8 7 152.3 83.5 14.8 29.8 0.5 8 152.9 85.4 14.5 30.1 0.66 9 154.9 85.9 14.1 30.6 0.8 10 152.2 79.8 17.1 ~~ 26.5 0.45 11 154.1 79.9 16.9 26.7 0.6 12 153.2 80.1 16.8 26.5 0.73 13 149.2 77.1 18.6 25.1 0.45 14 149.8 78.6 17.9 26.3 0.6 15 151.2 79.8 16.4 26.9 0.73 16 138.7 68.9 19.2 22.1 0.45 17 139.6 69.3 18.6 23.3 0.6 18 139.5 68.4 18.8 22.9 0.73 19 138.4 67.2 20.1 20.8 0.42 20 139.6 69.4 19.4 22.1 0.55 21 142.1 70.1 19.2 21.9 0.67 22 131.2 62.1 20.3 20.2 0.42 23 132.4 63.1 19.9 20.9 0.55 24 135.1 66.1 19.1 21.3 0.67 25 126.4 59.6 22.4 19.4 0.42 26 129.1 59.8 21.7 19.9 0.55 27 132.5 62.1 20.1 20.5 0.67 Please refer again Figures 2 and 3, which show the golf club head alloy of the present invention after casting, The metallographic structure of the alloy material after etching with 10 g of K3Fe(CN)6 + l〇g KOH + 100 ml of H20 etching solution. The first and second figures are respectively a microstructure of 200 times and 500 times magnification of the alloy of the present invention, and it can be seen that it is Fe-containing three-phase coexistence of ferrite iron, Ostian iron and Ma Tian iron. Cr-Ni alloy, which has the characteristics of three-phase strength and ductility. It can be verified that the alloy of this case can make the alloy have the structure of three-phase coexistence of ferrite iron, Osbate iron and 麻田散铁 through proper control of the steel/record ratio. ^'' As indicated, the golf club head alloy of the present invention is made of a specific ratio of 201228689 copper/nickel ratio to reduce the hardness, tensile strength and strength of the alloy. The club head has the advantage of easy cornering. '11 The golf club head alloy of the present invention is made of a steel/nickel ratio of a specific ratio such that the alloy has both a Worthfield iron phase, a ferrite phase, and a granulated iron phase. - The golf club head alloy of the present invention is produced by adjusting a specific copper/record ratio to produce the aforementioned three-phase non-ferrous steel alloy having a low hardness. While the invention has been described in connection with the preferred embodiments described above, it is not intended to limit the scope of the invention. The technical scope of the invention is protected, and therefore the scope of the invention is defined by the scope of the appended claims. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a flow chart of a method for producing a golf club head alloy of the present invention. Figure 2: Metallographic structure of the golf club head alloy of the present invention (200 times). Figure 3: Metallographic structure of the golf club head alloy of the present invention (500 times). [Main component symbol description]
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