200539972 九、發明說明： 【發明所屬之技術領域】 本發明係關於-種燒結體及其製造方法，尤其是關於_種以細粉為原 料之燒結體所用燒結硬化型粉末之組成及其製造燒結體之方法。 【先前技術】 粉末冶金合金設計一直是粉末冶金技術發展的起始環節，藉由各種合 金元素及不同含量的添加組合’可發展出各種合金鋼，應用於不同場合。 一般粉末冶金零件為符合其應用領域通常需具備有好的機械性質，因此零 件常必須施以淬火、回火之硬化熱處理以達到優良之機械性質。 然而淬火時由於冷卻速率快，零件易產生變形、尺寸不穩定、淬裂等 問題，且熱處理亦增加生產成本，故近年來已有燒結硬化型之粉末出現， 在粉末中添加Mo、Ni、Mn、Cr等高硬化能合金元素，使在以傳統壓結方 式壓出胚體後’將生胚燒結即可得到HRC30以上之硬度，例如H〇egames 公司之 Ancorsted 737SH (Fe-0_42Mn_1.40Ni_1.25M〇_C)或 Quebec 公司之 AT()MET4701(Fe_0_45Mn_a9_K)0M〇-0.45Cr-C)等。這些材料所製成之 零件在燒結細鱗分賴社之冷卻速率冷卻，可產生麻田散鐵及 變動鐵。雖然這些粉末經一般業者所常用之112(rc燒結3〇_4〇分鐘後其合 金元素成分仍不易均質化’但在相同密度及燒結處理條件下，不需施以泮 火硬化處理魏結後之機雛質已比―般雜結硬化型之合金為佳。燒結 硬化型合金雖節省燒結後熱處理成本，不過為符合快速冷卻速率之要求， 仍需在原有燒結爐改裝，增加特殊設計之高冷卻速率設備，甚至改用全新 之燒結爐，此方式仍造成額外之設備成本。此外，赠程之冷卻速率雖遠 200539972 季父洋火慢，但仍相當快，零件仍易有變形、尺寸不穩定、淬裂等缺點。又 如美國專利us娜88乃將該專利之粉末以傳統壓結方式壓出生胚後於 ⑽-⑵此之間燒結，然後以5_2〇t/分之冷卻速率即可達到燒結硬化效 果，改進了以往約贼/分以上之高冷卻速率，但該專利揭露之機械性質仍 不佳，特別是滅方面。以乾壓成職程而言，美國粉末冶金協會在細 年版之標準巾已魏結硬化型合金，其巾機齡録佳者為FLNC—侧 (1.0-3.0〇/〇Ni，0.65-0.950/oMo « l.〇.3.〇〇/oCu , 〇.6.〇.9〇/〇c , , 在燒結硬化並敎祕7.2 gW之贿下之拉賴射達9雇…硬度可 達HRC 30 ’但延性僅㈣，此乾壓型合金雖為燒結硬化型，但機械性質仍 不佳。就粉末冶金技術領域來說，細粉常用於金屬射出成形製程，金屬射 出成形技術所使用的粉末較傳統粉末冶金製程(乾壓與燒結)細，粒徑約在 30μηι以下，而乾壓用粉末粒徑約在15〇μιη以下，由於細粉對合金元素而 言擴散距離短，所以可以使添加之合金元素均勻擴散於基材中，因此以細 粉燒結之零件比傳統乾壓成形燒結零件具有較佳之機械性質。目前金屬粉 末射出成形㊉用合金為Fe-Ni-Mo-C系列合金，例如美國粉末冶金協會 (Metal Powder Industries Federation)所公佈之眾標準中機械性質最佳之 MIM-4605(1.5-2.5%Ni，0·2·0·5%Μο，0.4_0.6%C，<1.0%Si，餘鐵），此合金 在燒結後之拉伸強度可達415MPa，硬度可達HRB62，伸長率為15%，若 要達到此材料之最佳機械性質則必須將燒結後之產品施以淬火、回火等燒 結後熱處理，其拉伸強度可達1655MPa，硬度可達HRC48，伸長率為2·〇%。 雖然目前金屬射出成形工件已可藉燒結後熱處理而得到優良之機械性質， 200539972 但就金屬射出成形工件㈣，其熱處理成本佔其製造成本相當大之比例， 如何降低其熱處理成本為-重要課題，且由美崎末冶金齡所示資料及 各研究報導顯示’目前尚無應用於金屬粉末射出成形之燒結硬化型合金。 如上所述，使用細粉可改善合金元素之均質化，提高辑之機械性 、但^統乾壓製程使用細粉有一大問題，亦即細粉流動性不佳，益 入模穴中’因此無法以自動成形機成形，但此問題可藉造粒&程使 集成較大祕且成球形舒以克服，因此細粉仍應可使·乾壓成 【發明内容】 有鑑於此，本發明的主要目的係提供一種新的粉末組成，其粉末直徑 介於0.1〜30卿，使以粉末冶金方法製造出的燒結體有高的硬化能（即燒結 硬化型合金），使於燒結後於一般之降溫速率(3_2〇〇c/min)在傳統燒結爐中冷 卻即可得職好之顧性質，其巾錄賴之成分包含鐵、碳、鎳以及至 少-種以上之強化元素，其比例以重量百分比表示為鎳含量：3G_m 碳含量·· 0.1-0.8%，強化元素之總含量·· 〇·5_7%，剩餘為鐵含量，強化元素 係為Mo、〇、Cu、Ti、Α卜Mn、Si、ρ任一種。而碳係由添加之石墨粉或 含碳之Μ基鐵騎提供。此粉末組紅燒結體，不需經淬火處理即具有拉 伸強度大於1450MPa、硬度大於HRC38及伸長率大於1%之特性。 本發明的另一個目的係提供一種金屬射出成形製造方法，將上述燒結 硬化型金屬粉末組成應用於金屬射出成形，其生胚經燒結步驟後可不經淬 火之熱處理而僅以低溫回火處理即可達到良好之機械性質，其方法包括下 列步驟： 提供粉末及黏結劑，其中該粉末係使用直徑〇1〜3〇μηι的元素粉或合 200539972 金粉末， 混煉粉末及黏’錄末與減劑的混合成射料； 施以射出成形製程，將射料於射出成形機中射出而得生胚； 將生胚脫脂，以去除黏結劑； 將脫脂後之胚體於燒結爐中燒結及冷卻，其中燒結爐係為一般金屬粉 末射出成形業者常用之燒結爐，例如：真空爐或連續爐，且爐内之冷 卻速率約3-20°C/分；以及 後燒結熱處理，即低溫回火處理，其中回火溫度為⑼至峨，回 火時間為0.5至5小時。 本發明的另—個目的絲供—種傳紐末冶金製造方法，將上述燒結 硬化型金屬粉末組成應祕傳統粉末冶金製程（乾壓、燒結），其生胚經燒 結步驟後可秘較之鱗_僅龍溫回域轉可相陕之機械^ 質，其方法包括下列步驟： 提供粉末及雜劑，其中錄末係個直徑gi〜3g卿的元素粉或合 金粉末； 施以粉末造粒’使細粉絲結劑結合而成較大且具流動性的球形粉粒 aA · 體， 過篩，以選擇適當的粗粉供成形機使用； 施以成形製程’將粉末填人模穴巾壓結而得生胚； 將生胚脫脂，以去除黏結劑； 爐係為一般傳統粉 將脫脂後之胚體於燒結爐中燒結及冷卻，其中燒結 200539972 末冶金業者常用之燒結爐，例如：真空爐或連續爐，且爐内之冷卻速 率約3_20°C/分；以及 後燒結熱處理，即低溫回火處理，其巾社溫麟⑼至伽。c，回 火時間為0.5至5小時。 使用經造粒過之細粉再配合本發明之燒結硬化合金成分，則以乾壓製 程可製作出不須經淬域處理，燒結後即可得到優良機械性質之零件。 因此本發明之主要特徵在於設計—細粉燒結硬化型合金配方應用於 金^射出成形製程或傳統粉末冶金製程（乾壓、燒結），可使其蹲於較低 生n下，製造出具有高強度、高密度、高硬度及韋刃性佳之燒結體成品。 【實施方式】 以下將參照表1及表2之燒結體元素成分和機械性f，其中表2之例 1-4為金屬射出成形方法所製得之燒結體性f，表2之例5為傳統粉末冶金 方法所製狀齡舰f ’^聽2說明本發明之燒賴元素成分及 其裝k方法’其中例1至例5為本發明’例a至例D為對照組，乃現有文 獻報導中之資料。 例A :以美國粉末冶金協會MpiF_35標準中射出成形用之mim娜之成 刀（見表1)所製付燒結品之機械性質，如表2所示。 例B:同例a，但產品經過熱處理後機械性質大幅改善，如表2所示。 例c ·以美國粉末冶金協會MPIF_35標準中射出成形用之臟⑶⑻之成 分(見表1)所製得燒結品之機械性質，如表2所示。 例D ·以美國粉末/纟金齡MpiF_35鮮巾傳絲顧形狀凡勝權8 之成刀（見表1)所製得燒結品之機械性質，如表2所示。 200539972 例1 :以表1之成分將0·1-30μιη之各種所需成分之粉末與7wt%之黏結劑， 於Z型高剪力混煉機以15G°C混煉-小時後冷卻，以得觸粒狀之射料，將 此射料投入射出機中製作拉伸試棒(美國粉末冶金協會MpiF 5〇之標準試 棒）’射出後之试棒以工業界習用之脫脂步驟脫脂，如以正庚烧於⑽它溶劑 脫月曰5小日守’然後於真空燒結爐中以每分鐘5°c之升溫速率由室溫升至650 C並持溫一小時，隨後再以每分鐘l〇°C之速率升至i2〇〇°c，再於12〇〇〇c燒 結一小時後以爐冷方式降溫冷卻，不需經熱處理，即可得到HRC51之硬度 及1.0%之延性。經180°C回火兩小時，可改善延性而得到18〇〇Mpa之強度， HRC45之硬度及3.0%之延性，如表2所示。經以掃描式電子顯微鏡觀察破 斷面後亦可看到酒窩狀之延性組織(如圖一）’顯示由此合金成分可得到且高 強度、高硬度且延性佳之產品。相較於美國粉末冶金協會射出成形工件中 機械性質最佳者為MIM-4605，此MIM-4605若未經熱處理的話僅有 415MPa，HRB62，及15%之延性，如表2之例A所示。若經淬火、回火熱 處理者，其性質為1655MPa，HRC48及2%之延性，，如表2之例B所示。 故MIM-4605需經淬火硬化處理方可達到與本發明之燒結體之機械性質相 近之結果(無須淬火硬化處理）。 200539972 表1本發明之例1至例6及美國粉末冶金協會MPIF標準及業界習用之例 A至例D之成分（以重量百分比表示） 元素 例1 例2 例3 例4 例5 例6 例A及B 例C 例D 碳 0.36% 0.34% 0.4% 0.45% 0.5% 0.4% 0.4-0.6% <0.1% 0.6-0.9% 鎳 8.0% 9.0% 8.0% 4.5% 8.0% 7.5% 1.5-2.5% 6.5-8.5% 1.0-3.0% 鉬 0.8% 0.8% 1.0% 1.0% 0.8% 0.8% 0.2-0.5% [<05% 0.65-0.95% 鉻 0.8% 0.8% 0.8% 0.5% 0.8% 0.5% - - _ 锰 0.6% - - - - 銅 1.5% 0.5% - - - 1.0-3.0% 矽 0.3 0.3 0.3 0.3 0.3% 0.3% <1.0 <1.0 - 鐵 餘 餘 餘 餘 餘 餘 餘 餘 餘 表2例1至例6之合金與例A至例D之合金機械性質之比較 例 密度（g/cm3) 淬火硬化處理 拉伸強度（MPa) 硬度 伸長率^' A 7.5 無 415 HRB62 B 7.5 有* 1655 HRC48 飞 C 7.6 無 440 HRB69 D 7.2 無 970 HRC30 1.0 ^^- 1 7.6 1800 HRC45 1 ^^- 2 7.6 無1 1780 HRC45 3 7.6 1720 HRC46 4 4 7.5 無1 1450 HRC38 1 5 7.5 1690 HRC47 3^—— 6 7.5 無1 1650 HRC43 1 *860°C奥斯田鐵化後油淬火，再於180°C回火2小時 11 1 燒結後於180°C回火2小時 200539972 例2 :如同例1之製程，但成分改為以表丨中所示例2之成分，所製得試棒 經回火後之強度可達1780MPa之拉伸強度，hrcm之硬度及4%之延性。 例3 :如同例1之製程，但成分改為表！中所示例3之成分，所得試棒經回 火後可達1720MPa之強度，HRC46之硬度及4%之伸長率。 例4 ·如同例1之製程，但成分改為表！中所示例4之成分，所得試棒經回 火後可達1450MPa之強度，HRC38之硬度及4%之伸長率。 例5 :以表1中例5之成分將〇·ι_30μηι之各種所需成分之粉末與丨加％之 黏結劑，經喷霧造粒步驟，將細粉與水和黏結劑如聚乙烯醇等混合攪拌成 泥漿狀，經由喷嘴高速喷出，喷出物受熱空氣或熱氮氣吹襲，使得其中之 水分蒸發射伽粉與結合成粒度較大直徑約40μηι JL具流動性的球 形粗粉，將粗粉填入模穴中經自動成形機壓結成形而得生胚試棒，成形後 之試棒以工業界習用之脫脂步驟脫脂，如以每分鐘5〇c之升溫速率由室溫升 至400°C後，再以每分鐘3。(：之速率升至11〇(rt，持溫一小時，然後以每分 鐘l〇°C之速率升至120(TC，再於120(rc燒結一小時後以爐冷方式降溫冷 卻’不需經淬火熱處理，只需經180°C回火兩小時，即可得到169〇MPa之 強度HRC47之硬度及3.0%之延性，如表2戶斤示。顯示由此合金成分可得 到具高強度、高硬度且延性佳之產品。相較於類粉末冶金協會乾壓成形 結構工件中機械性質最佳之燒結硬化合金為FLNC-4408，此FLNC-4408僅 有970MPa ’ HRC30 ’及ι·〇%之延性，如表2之例d所示。 12 200539972 例6 :如同例5之製程，但成分改為以表1中所示例6之成分，所製得試棒 經回火180°C兩小時後之強度可達i600MPa之拉伸強度，HRC43之硬度及 4%之延性。 綜上所述，相較於美國粉末冶金協會(MetalP〇wderIndustries Federation，MPIF)所列經過淬火、回火處理後之射出成形最佳合金 (MIM-4605)及乾壓成形結構件之最佳燒結硬化合金（FLNC_44〇8)，本發明 之燒結硬化型合金，除具有不需淬火硬化處理即可達到相似甚至更佳之機 械性質外，並可避免因淬火硬化所衍生之零件易產生變形、尺寸不穩定、 淬裂等問題，且可節省淬火熱處理之生產成本。對於射出成形而言，本發 明乃首見之燒結硬化型合金，而對於傳統粉末冶金之壓結製程雖有所謂之 燒結硬化型合金，但其粉末合金配方所製之燒結體所需冷卻速率比本發明 為快，工件較易變形，且機械性質不佳。故本發明所揭示之内容兼具優良 之機械性質、尺寸穩定性與低成本等優點。 雖然本發明已以較佳實施例揭露如上，然其並非用以限定本發明，任 何熟習此技術者，在不脫離本發明之精神和範圍内，當可作些許之更動盘 潤飾，因此本發明之保護範圍當視後附之申請專利範圍所界&者為準。 【圖式簡單說明】 圖一：以掃描式電子顯微鏡觀察例1試片之破斷面，可看到 延性組織。 卜。 【主要元件符號說明】 無 13200539972 IX. Description of the invention: [Technical field to which the invention belongs] The present invention relates to a kind of sintered body and its manufacturing method, in particular to a composition of sintered hardened powder for sintered body using fine powder as raw material and its manufacturing and sintering System. [Previous technology] The design of powder metallurgy alloys has always been the starting point of the development of powder metallurgy technology. Through the addition of various alloying elements and different contents, various alloy steels can be developed and applied to different occasions. Generally, powder metallurgy parts must have good mechanical properties in order to meet their application fields. Therefore, parts must often be subjected to hardening and tempering hardening heat treatment to achieve excellent mechanical properties. However, due to the rapid cooling rate during quenching, parts are prone to problems such as deformation, unstable dimensions, and cracking, and heat treatment also increases production costs. Therefore, sinter-hardening powders have appeared in recent years. Mo, Ni, and Mn are added to the powder. High hardening energy alloy elements such as Cr, Cr, etc., so that the hardness of HRC30 or higher can be obtained by sintering the green embryo after extruding the embryo body in the traditional compaction method. For example, Ancorsted 737SH (Fe-0_42Mn_1.40Ni_1.25M) 〇_C) or AT () MET4701 (Fe_0_45Mn_a9_K) 0M0-0.45Cr-C) of Quebec company. The parts made of these materials are cooled at the cooling rate of the sintered fine scale branch, which can produce Asada loose iron and fluctuating iron. Although these powders are still difficult to homogenize after 112 (rc sintering for 30-40 minutes), which are commonly used by ordinary practitioners, under the same density and sintering treatment conditions, it is not necessary to apply the sintering hardening treatment. The quality of the brood is better than that of the ordinary heterojunction hardened alloy. Although the sintered hardened alloy saves the cost of heat treatment after sintering, it still needs to be modified in the original sintering furnace in order to meet the requirements of rapid cooling rate and increase the high cooling rate of the special design. The equipment, even the use of a new sintering furnace, this method still causes additional equipment costs. In addition, the cooling rate of the gift fare is slower than 200539972, but it is still quite fast. Parts are still prone to deformation, unstable dimensions, Disadvantages such as quench cracking. Another example is the US patent usna 88, which sinters the powder of this patent in the traditional compaction method and then sinters between ⑽ and ⑵, and then achieves sintering at a cooling rate of 5_20t / min. The hardening effect improves the previous high cooling rate of about thief per minute, but the mechanical properties disclosed by this patent are still not good, especially in terms of destruction. In terms of dry pressing, American powder The standard metal towels of the Metallurgy Association in the year-old version have been made of hardened alloy. The best record of the machine age is FLNC-side (1.0-3.0〇 / 〇Ni, 0.65-0.950 / oMo «1.0.0.3.〇〇 / oCu, 〇.6.0.〇.〇〇 / 〇c,, Lai Lai shot up to 9 hours under the sintering hardening and secret 7.2 gW bribe ... hardness up to HRC 30 'but ductility is only ㈣, this dry pressing type Although the alloy is sinter-hardened, its mechanical properties are still poor. As far as powder metallurgy is concerned, fine powder is often used in metal injection molding processes. The powder used in metal injection molding technology is more traditional than powder metallurgy (dry pressing and sintering). Fine, the particle size is about 30μηι or less, and the powder size for dry pressing is about 150μιη or less. Since the fine powder has a short diffusion distance to the alloy elements, the added alloy elements can be uniformly diffused in the substrate, so Fine powder sintered parts have better mechanical properties than traditional dry-pressed sintered parts. At present, the metal powder injection molding alloy is Fe-Ni-Mo-C series alloys, such as the Metal Powder Industries Federation. The best mechanical properties among the published standards MIM-4605 (1.5-2.5% Ni, 0 · 2 · 0 · 5% Μο, 0.4_0.6% C, < 1.0% Si, residual iron), the tensile strength of this alloy after sintering can reach 415MPa, The hardness can reach HRB62 and the elongation is 15%. To achieve the best mechanical properties of this material, the sintered product must be subjected to heat treatment such as quenching and tempering. The tensile strength can reach 1655MPa and the hardness can reach HRC48, with an elongation of 2.0%. Although metal injection molded workpieces can now be obtained with excellent mechanical properties by heat treatment after sintering, 200539972, for metal injection molded workpieces, the heat treatment cost accounts for a considerable proportion of its manufacturing cost. How to reduce the cost of heat treatment is an important issue, and according to the data and various research reports shown by Misaki ’s metallurgical age, 'at present, there is no sinter-hardening alloy used for metal powder injection molding. As mentioned above, the use of fine powder can improve the homogenization of alloying elements and improve the mechanical properties of the alloy. However, the use of fine powder in the dry pressing process has a major problem, that is, the fine powder has poor fluidity and benefits into the cavity. It cannot be formed by an automatic forming machine, but this problem can be overcome by the granulation & process to make the integration larger and spherical, so the fine powder should still be able to be dry-pressed. [Invention] In view of this, the present invention The main purpose is to provide a new powder composition with a powder diameter of 0.1 to 30 μm, so that the sintered body produced by powder metallurgy has a high hardening energy (ie, sinter-hardened alloy). The cooling rate (3_2〇c / min) can be obtained by cooling in a traditional sintering furnace. Its ingredients include iron, carbon, nickel and at least one or more strengthening elements. The proportion is based on The weight percentage is expressed as nickel content: 3G_m carbon content. 0.1-0.8%, total content of strengthening elements. 0.5-7%, the rest is iron content, and the strengthening element system is Mo, O, Cu, Ti, A, Mn, Either Si or ρ. The carbon is provided by added graphite powder or carbon-containing M-based iron riders. This powder group red sintered body has the characteristics of tensile strength greater than 1450 MPa, hardness greater than HRC38, and elongation greater than 1% without quenching. Another object of the present invention is to provide a metal injection molding manufacturing method in which the above-mentioned sinter-hardening type metal powder composition is applied to metal injection molding. After the sintering step, the green embryo can be subjected to low-temperature tempering without quenching heat treatment. To achieve good mechanical properties, the method includes the following steps: Provide a powder and a binder, wherein the powder is an element powder with a diameter of 0 ~ 30 μηι or a 200539972 gold powder, a mixed powder and a paste The raw material is injected into an injection molding machine to obtain a green embryo; the green embryo is degreased to remove the binder; the degreased embryo body is sintered and cooled in a sintering furnace, The sintering furnace is a sintering furnace commonly used by general metal powder injection molding industry, such as: vacuum furnace or continuous furnace, and the cooling rate in the furnace is about 3-20 ° C / min; and post-sintering heat treatment, that is, low temperature tempering treatment, Among them, the tempering temperature is ⑼ to E, and the tempering time is 0.5 to 5 hours. Another purpose of the present invention is to provide a method of wire metallurgy manufacturing. The above-mentioned sinter-hardened metal powder is composed of a traditional powder metallurgy process (dry pressing, sintering), and the green embryo can be compared with the sintering step. Scale_Only Longwen returns to the field to transform the mechanical quality of Shaanxi. Its method includes the following steps: Provide powder and miscellaneous agents, where the end is a element powder or alloy powder with a diameter of gi ~ 3g Qing; powder granulation 'Combine the fine vermiculite to form a large and fluid spherical powder aA · body, sieve to select the appropriate coarse powder for the forming machine; apply the forming process' to fill the powder into the mold cavity towel Raw embryos are formed; the raw embryos are degreased to remove the binder; the furnace is a conventional powder that sinters and cools the degreased embryos in a sintering furnace, including sintering 200539972, a sintering furnace commonly used by metallurgists, such as: vacuum Furnace or continuous furnace, and the cooling rate in the furnace is about 3-20 ° C / min; and post-sintering heat treatment, that is, low temperature tempering treatment, its towels are warm and warm. c. Tempering time is 0.5 to 5 hours. Using the granulated fine powder in combination with the sinter-hardened alloy composition of the present invention, a dry pressing process can be used to produce parts that do not need to be quenched and can be obtained with good mechanical properties after sintering. Therefore, the main feature of the present invention is that the design-fine powder sinter-hardening alloy formula is applied to the gold injection molding process or the traditional powder metallurgy process (dry pressing, sintering), which can make it squat under lower production n, and produce a high Finished sintered body with good strength, high density, high hardness, and good cutting edge. [Embodiment] The sintered body element composition and mechanical properties f of Table 1 and Table 2 will be referred to below, in which Examples 1-4 of Table 2 are sintered body properties f obtained by the metal injection molding method, and Example 5 of Table 2 is The conventional powder metallurgy method f ^ ^ 2 is used to explain the composition of the burning element and the method of loading the method according to the present invention, wherein Examples 1 to 5 are the present invention, and Examples a to D are the control group, which is the existing literature. Information in the report. Example A: The mechanical properties of the sintered products made by the Mim Na knife (see Table 1) used for injection molding in the American Powder Metallurgy Association MpiF_35 standard are shown in Table 2. Example B: Same as Example a, but the mechanical properties of the product are greatly improved after heat treatment, as shown in Table 2. Example c • The mechanical properties of the sintered product obtained by injection of the dirty CD⑻ components (see Table 1) for forming in the American Powder Metallurgy Association MPIF_35 standard are shown in Table 2. Example D · The mechanical properties of the sintered product produced by the American powder / Golden Age MpiF_35 fresh towel pass through the shape of Gu Shengquan 8 (see Table 1), as shown in Table 2. 200539972 Example 1: Use the ingredients in Table 1 to mix powders of various required components from 0.1 to 30 μm and 7 wt% of a binder in a Z-type high-shear mixer at 15G ° C for one hour, then cool to To obtain granular shots, put the shots into an injection machine to make tensile test rods (standard test rods of the American Powder Metallurgy Association MpiF 50). After the injection, the test rods are degreased using the degreasing step commonly used in the industry, such as Take n-heptane as a solvent and remove the solvent for 5 days, then raise the temperature in the vacuum sintering furnace from room temperature to 650 C at a temperature of 5 ° c per minute and hold the temperature for one hour. The rate of 0 ° C is increased to i200 ° c, and then sintered at 12,000c for one hour, and then cooled in a furnace cooling manner. Without heat treatment, the hardness of HRC51 and the ductility of 1.0% can be obtained. After tempering at 180 ° C for two hours, the ductility can be improved to obtain the strength of 18000Mpa, the hardness of HRC45 and the ductility of 3.0%, as shown in Table 2. After observing the fractured surface with a scanning electron microscope, a dimple-like ductile structure (see Fig. 1) can be seen. It shows that the alloy component can be obtained from this alloy component and has high strength, high hardness, and good ductility. Compared to the American Powder Metallurgy Association injection molding workpiece with the best mechanical properties is MIM-4605, this MIM-4605 has only 415MPa, HRB62, and 15% ductility if not heat treated, as shown in Example A of Table 2 . If it is quenched and tempered, its properties are 1655 MPa, HRC48 and 2% ductility, as shown in Example B in Table 2. Therefore, MIM-4605 needs to be quenched and hardened to achieve results similar to the mechanical properties of the sintered body of the present invention (no quenching and hardening required). 200539972 Table 1 Compositions of Examples 1 to 6 of the invention and Examples A to D of the American Powder Metallurgy Association MPIF Standard and Industry Conventions (expressed as weight percentages) Element Example 1 Example 2 Example 3 Example 4 Example 5 Example 6 Example A Case B Case C Case D Carbon 0.36% 0.34% 0.4% 0.45% 0.5% 0.4% 0.4-0.6% < 0.1% 0.6-0.9% Nickel 8.0% 9.0% 8.0% 4.5% 8.0% 7.5% 1.5-2.5% 6.5- 8.5% 1.0-3.0% Molybdenum 0.8% 0.8% 1.0% 1.0% 0.8% 0.8% 0.2-0.5% [< 05% 0.65-0.95% Chromium 0.8% 0.8% 0.8% 0.5% 0.8% 0.5%--_ Manganese 0.6 %----Copper 1.5% 0.5%---1.0-3.0% Silicon 0.3 0.3 0.3 0.3 0.3% 0.3% < 1.0 < 1.0-Iron surplus surplus surplus surplus surplus Table 2 Examples 1 to 6 Comparative Examples of Mechanical Properties of Alloys and Alloys of Examples A to D Density (g / cm3) Quenching Hardening Tensile Strength (MPa) Hardness Elongation ^ 'A 7.5 No 415 HRB62 B 7.5 Yes * 1655 HRC48 Fly C 7.6 None 440 HRB69 D 7.2 None 970 HRC30 1.0 ^^-1 7.6 1800 HRC45 1 ^^-2 7.6 None 1 1780 HRC45 3 7.6 1720 HRC46 4 4 7.5 None 1 1450 HRC38 1 5 7.5 1690 HRC47 3 ^ —— 6 7.5 None 1 1650 HRC43 1 * 860 ° C After Austen Ironized Oil Quenched and then tempered at 180 ° C for 2 hours 11 1 After sintering, tempered at 180 ° C for 2 hours 200539972 Example 2: The process is the same as that of Example 1, but the composition is changed to the component of Example 2 shown in Table 丨. The strength of the test rod after tempering can reach the tensile strength of 1780MPa, the hardness of hrcm and the ductility of 4%. Example 3: The process is the same as in Example 1, but the composition is changed to table! As shown in the composition of Example 3, the obtained test rod after tempering can reach a strength of 1720 MPa, a hardness of HRC46 and an elongation of 4%. Example 4 · The process is the same as in Example 1, but the composition is changed to table! As shown in the composition of Example 4, the obtained test rod after tempering can reach a strength of 1450 MPa, a hardness of HRC38 and an elongation of 4%. Example 5: Use the ingredients of Example 5 in Table 1 to mix powder of various required ingredients with a concentration of 0.005-30 μηι and add ％ binding agent. After spraying and granulating, mix the fine powder with water and a binding agent such as polyvinyl alcohol. Mix and stir into a slurry, and spray it at high speed through a nozzle. The sprayed material is blown by hot air or hot nitrogen, so that the water in it evaporates and sprays powder and combines to form a spherical coarse powder with a larger particle size of about 40 μηι. The coarse powder is filled into the cavity and compacted by an automatic forming machine to obtain a green embryo test rod. The formed test rod is degreased by a conventional degreasing step in the industry, such as rising from room temperature to 50 ° C per minute. After 400 ° C, start again at 3 per minute. (: The rate is increased to 11 ° (rt, holding temperature for one hour, and then to 120 ° C at a rate of 10 ° C per minute, and then cooled at 120 ° C in an oven cooling method for one hour after sintering for one hour.) After quenching and heat treatment, it only needs to be tempered at 180 ° C for two hours to obtain the hardness of HRC47 with a strength of 1690 MPa and the ductility of 3.0%, as shown in Table 2. The alloy composition can be obtained with high strength, A product with high hardness and good ductility. Compared to the powder metallurgy association, the sinter-hardened alloy with the best mechanical properties in dry-formed structural workpieces is FLNC-4408. This FLNC-4408 has a ductility of only 970 MPa 'HRC30' and ι · 〇%. , As shown in Example d of Table 2. 12 200539972 Example 6: The process is the same as that of Example 5, but the composition is changed to the composition of Example 6 shown in Table 1. The test rods produced are tempered at 180 ° C for two hours. The strength can reach the tensile strength of i600MPa, the hardness of HRC43 and the ductility of 4%. In summary, compared with the injection molding after quenching and tempering listed by the American Powder Metallurgy Association (MPIF) The best alloy (MIM-4605) and the best sinter hardening of dry-formed structural parts (FLNC_44〇8), in addition to the sinter-hardening alloy of the present invention, it can achieve similar or better mechanical properties without the need for quenching and hardening, and can prevent parts derived from quenching and hardening from being easily deformed, dimensionally unstable, Problems such as quench cracking, and can save the production cost of quenching heat treatment. For injection molding, the present invention is the first sinter-hardened alloy, and for the traditional powder metallurgy compaction process, there are so-called sinter-hardened alloys, but The required cooling rate of the sintered body made of the powder alloy formula is faster than the present invention, the workpiece is more easily deformed, and the mechanical properties are not good. Therefore, the content disclosed by the present invention has both excellent mechanical properties, dimensional stability and low cost. Although the present invention has been disclosed in the preferred embodiment as above, it is not intended to limit the present invention. Anyone skilled in the art can make some modifications to the touch screen without departing from the spirit and scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the scope of the appended patent application scope. [Schematic description of the diagram] Figure 1: Scanning Observation of the fracture surface of the test piece of Example 1 with an electron microscope reveals the ductile structure. Bl. [Description of Symbols of Main Components] None 13