燈座注塑模具設計

燈座注塑模具設計,燈座,注塑,模具設計 附件1：外文資料翻譯譯文 噴射成形在模具注塑和壓鑄中的應用 摘要 快速凝固工藝（RSP）加工是一種適合生產(chǎn)塑型和模具的噴射成形技術(shù)。是在一個步驟中把快速凝固處理和net-shape材料加工相結(jié)合的方法。噴灑存放捕捉功能工具模式的能力消除了昂貴的加工工序常規(guī)模具制造，并減少了周轉(zhuǎn)時間。此外，快速凝固抑制碳化物析出和增長，讓許多鐵素體工具鋼人工老化，替代傳統(tǒng)的熱處理，提供了獨特的好處。材料性能和微觀結(jié)構(gòu)的轉(zhuǎn)變在熱處理的噴射成形工具鋼H13中有描述。 導言 塑型，模具，以及相關的工具是用來塑造許多我們在家里或在工作上每天使用的塑料和金屬部件。一個理想的加工的過程中一部分形狀（核心和腔）由偽造工具鋼或粗金屬鑄件鑄造，且增加冷卻渠道，孔，和其他機械的功能，其次是粉碎。許多模具經(jīng)過熱處理（ austenitization /淬火/回火）來改善鋼的性能，其次是最后的研磨和拋光，以達到理想的效果。常規(guī)制作模具是非常昂貴，費時的，因為： ⒈ 顧客定制，這反映了形狀和質(zhì)地要接近理想效果。 ⒉ 使用的材料難以用機器進行加工和工作。工具鋼行業(yè)需要員工長期的生產(chǎn)經(jīng)營。加工工具鋼需要加強設備資本，因為專門的設備往往需要個別加工步驟。 ⒊ 加工機械必須準確。往往由許多單獨部分組成，必須制造準確使得產(chǎn)品最終能正常工作。注塑模具的費用，隨規(guī)模和復雜性的不同，從10000美元到30000美元左右不等（美國） ，定貨到交貨的為3至6個月。工具檢查和部分資格可能需要額外的3個月。大型壓鑄模的傳輸和鈑金沖壓模具制造汽車車身面板可能耗資超過100萬美元（美國） 。交貨時間通常大于40周。大型汽車公司（美國）每年要投資約10億美元來生產(chǎn)新的元件，用于他們的新系列轎車和卡車中。噴射成形具有巨大的潛力，它能降低成本和交貨時間，它省略了研磨和拋光等步驟。此外，噴霧形成具有強有力的手段來控制隔離期間的合金元素凝固和碳化物的形成，并能創(chuàng)造有利的亞穩(wěn)相在許多常用工具鋼的鐵素體中。其結(jié)果是，熱處理可以用相對較低的溫度沉淀硬化來定制屬性，如硬度，韌性，熱疲勞阻力和力量。本文介紹了應用噴射成形技術(shù)生產(chǎn)H13的注塑模具和壓鑄應用，以及低溫熱處理的好處。 快速凝固工藝加工 快速凝固工藝（RPS）加工，是一種適合生產(chǎn)模具的噴射成形技術(shù)。是把快速凝固處理和net-shape材料加工結(jié)合為一個步驟的加工方法。轉(zhuǎn)換模具為圖形的一般概念是根據(jù)設計說明來用CAD文件勾畫出藍圖，使用合適的快速原型（反相）技術(shù)來確定主要的加工步驟，如光固化。根據(jù)圖形使用氧化鋁或石英來澆注一個陶瓷，（圖1 ） 。隨后再噴射一層工具鋼 （或其他合金）來獲取所需的形狀，表面紋理和細節(jié)。再將由此產(chǎn)生的金屬塊冷卻到室溫，之后將其分離。通常情況下，那層的外圍被作為一個泥框架來注入材料 。整個模具的制作周轉(zhuǎn)時間約3天。模具生產(chǎn)的這種方式已被用于原型和生產(chǎn)運行在注塑和壓鑄。 Figure 1. RSP Tooling? processing steps. 快速凝固工藝加工一個重要的好處是它允許在注塑前提早為一個部件作出設計流程。真正的做到配合零件評估的形式，使用相同的生產(chǎn)工藝計劃來進行原型制造。如果這部分是合格的，可在加工運行中將其作為常規(guī)的生產(chǎn)加工來使用。作為一個容易被修改的數(shù)字化數(shù)據(jù)庫和RP技術(shù)設計保存使用。 實驗程序 氧化鋁基陶瓷（ Cotronics 780 ）標準模具是用硅橡膠或主要用凍結(jié)鑄造。建立之后，陶瓷模型被演示，在窯中用火燒，并冷卻到室溫。 H13的工具鋼在氮保護氣的影響下，過熱約100 ℃后會熔化 ，壓力被送入到收斂/發(fā)散型噴霧嘴中。在惰性氣體中噴霧裝置飛行有最小的氧化霧化液滴，它們以200公斤/小時的速度沉積著。天然氣金屬質(zhì)量流率大約為0.5 。 對于拉伸性能和硬度評價，噴射成形材料切片使用線切割機并形成一個0.05毫米厚的熱影響區(qū)。每個樣本涂上BN且放置在一個密封的金屬箔包作為一項預防措施，以防止脫碳。人工樣本在溫度400至700 ℃中放置1小時，然后氣冷。常規(guī)熱處理H13的方法是將其放置于1010℃的austenitized中30分鐘。然后氣冷，最后以538℃雙重鍛煉（分別2小時）。 在室溫下使用島津M型維氏硬度測試法對顯微硬度進行測量時讀數(shù)緩慢的上升平均10小格。再使用奧林巴斯光學模型酯酶-3金相和Amray模型1830掃描電子顯微鏡觀測工具鋼的微觀結(jié)構(gòu)的蝕刻（ 3 ％ 尼特）。之后通過energydispersive能譜（EDS公司）對相組成進行分析 。使用Microtrac對overspray樣本的粒度分布進行全范圍分析，再用粉末粒子分析儀對200微米篩刪除粗片后，利用阿基米德定律和梅特勒余額對采樣密度進行評價（示范AE100）。 一種類似1-D計算機代碼開發(fā)的INEEL是用來評測多相流行為內(nèi)噴管和自由射流地區(qū)的。守則的基本數(shù)值解決了穩(wěn)態(tài)氣體流場通過自適應網(wǎng)格的問題，保守的變量的方法和治療液滴相在拉格朗日的方式充分的空氣動力學和精力充沛的耦合關系飛沫和運輸天然氣。液態(tài)金屬噴射系統(tǒng)天然氣動態(tài)，影響傳熱和墻摩擦也包括在內(nèi)。該代碼還包含一個非平衡凝固模型，允許滴過冷和復輝。這個代碼使得地圖的溫度和流速剖面的天然氣好平衡，且霧化液滴在噴嘴和自由射流地區(qū)中。 結(jié)果與討論 噴射成形是一個強大的快速模具制造技術(shù)，該技術(shù)使得工具鋼模具成為了一個簡單的生產(chǎn)方式。實例插入模具中給出了圖2 。噴射成形使用陶瓷部分格局產(chǎn)生反相。 Figure 2. Spray-formed mold inserts. (a) Ceramic pattern and H13 tool steel insert. (b) P20 tool steel insert. 粒子和氣體的運動 圖3是H13的工具鋼噴劑大規(guī)模的粒子質(zhì)量和累積頻率分布圖。許多通過中心點的直徑的插值被確定為56微米，大小相當于50 ％的累積量。意思是該地區(qū)平均直徑和數(shù)量的直徑計算分別為53微米和139微米。其幾何標準偏差為ód=(d84/d16)?， 圖3 表示在d84和d16的粒徑相應的84％和16％累積量為1.8。 Figure 3. Cumulative mass and mass frequency plots of particles in H13 tool step sprays. 圖4給出的計算結(jié)果為多相流場速度（圖4a）和H13工具鋼固體部分的內(nèi)部的自由射流噴嘴和地區(qū)（圖4b）。氣體的速度增加直到電擊前位置，之后它急劇下降，最終達到噴嘴腐爛指數(shù)以外。小水滴極可能用不規(guī)則速度運動，之后加快噴嘴內(nèi)部和外面減速。最終達到最后的速度。 眾所周知，噴射成形中的高顆粒冷卻速度在噴霧射流（103-106的K/s）和大量儲存粒子的復輝（1-100開/分）。大部分粒子造成堅實的部分約為0.75 。比計算固體分數(shù)概況?。▇30微米）且存在大型飛沫（~150微米）進入噴嘴中，如圖4b。噴射成形儲蓄 這種高熱量提取率降低侵蝕影響表面的工具模式。它可以配合適當?shù)墓に嚄l件將不大令人滿意的傳統(tǒng)的金屬鑄造工藝用于相對較軟的陶瓷材料澆注。 Figure 4. Calculated particle and gas behavior in nozzle and free jet regions. (a) Velocity profile.(b) Solid fraction. 精細表面細節(jié)可以成功地轉(zhuǎn)移到模式噴射成形模具。表面粗糙度依賴于成型表面的格局。泥漿鑄造商業(yè)生產(chǎn)的陶瓷表面粗糙度約為1微米，適用于許多成型。沉積工具在玻璃鋼板材的鏡面表面約為0.076微米。在如今的國家的發(fā)展中，三維重復性噴射成形模具有著共同的重要性。 化學 H13工具鋼的化學目的是使材料承受的溫度，壓力，磨損和熱循環(huán)能達到苛刻的要求，如模具鑄造。它是最流行的壓鑄合金和全球第二受歡迎的工具鋼的注塑。該鋼具有較低的碳含量(0.4 wt.%)，以促進韌性，和中等鉻含量(5 wt%) ，以提供良好的抗高溫軟化，1％的硅含量，以改善抗高溫氧化，小量的鉬，并且釩也有所增加（約1 ％），因此能形成穩(wěn)定的碳化物，增加抗沖蝕磨損。根據(jù)成分的分析，對H13的工具鋼前后噴射成形的結(jié)果總結(jié)在表1中，表明無顯著變化和合金補充。 微觀結(jié)構(gòu) H13工具鋼的大小，形狀，類型和分布的碳化物發(fā)現(xiàn)是取決于處理方法和熱處理。通常的商業(yè)鋼加工是在軋機退火條件和熱處理（austenitized /淬火/回火）之前使用的。典型的方法是在高達1010℃的austenitized中處理，后在空氣中或油中進行淬火，并以540至650℃進行認真鍛煉兩次或三次，直到獲得所需的結(jié)合硬度，熱疲勞抗力，和韌性。  INEEL CON 2000 00104 PREPRINT Spray Formed Tooling for Injection Molding and Die Casting Applications K M McHugh B R Wickham June 26 2000 June 28 2000 International Conference on Spray Deposition and Melt Atomization This is a preprint of a paper intended for publication in a journal or proceedings Since changes may be made before publication this preprint should not be cited or reproduced without permission of the author This document was prepared as a account of work sponsored by an agency of the United States Government Neither the United States Government nor any agency thereof or any of their employees makes any warranty expressed or implied or assumes any legal liability or responsibility for any third party s use or the results of such use of any information apparatus product or process disclosed in this report or represents that its use by such third party would not infringe privately owned rights The views expressed in this paper are not necessarily those of the U S Government or the sponsoring agency BECHTEL BWXT IDAHO LLC 1 Spray Formed Tooling For Injection Molding and Die Casting Applications Kevin M McHugh and Bruce R Wickham Idaho National Engineering and Environmental Laboratory P O Box 1625 Idaho Falls ID 83415 2050 e mail kmm4 inel gov Abstract Rapid Solidification Process RSP Tooling is a spray forming technology tailored for producing molds and dies The approach combines rapid solidification processing and net shape materials processing in a single step The ability of the sprayed deposit to capture features of the tool pattern eliminates costly machining operations in conventional mold making and reduces turnaround time Moreover rapid solidification suppresses carbide precipitation and growth allowing many ferritic tool steels to be artificially aged an alternative to conventional heat treatment that offers unique benefits Material properties and microstructure transformation during heat treatment of spray formed H13 tool steel are described Introduction Molds dies and related tooling are used to shape many of the plastic and metal components we use every day at home or at work The process involves machining the negative of a desired part shape core and cavity from a forged tool steel or a rough metal casting adding cooling channels vents and other mechanical features followed by grinding Many molds and dies undergo heat treatment austenitization quench temper to improve the properties of the steel followed by final grinding and polishing to achieve the desired finish 1 Conventional fabrication of molds and dies is very expensive and time consuming because Each is custom made reflecting the shape and texture of the desired part The materials used to make tooling are difficult to machine and work with Tool steels are the workhorse of industry for long production runs Machining tool steels is capital equipment intensive because specialized equipment is often needed for individual machining steps Tooling must be machined accurately Oftentimes many individual components must fit together correctly for the final product to function properly 2 Costs for plastic injection molds vary with size and complexity ranging from about 10 000 to over 300 000 U S and have lead times of 3 to 6 months Tool checking and part qualification may require an additional 3 months Large die casting dies for transmissions and sheet metal stamping dies for making automobile body panels may cost more than 1million U S Lead times are usually greater than 40 weeks A large automobile company invests about 1 billion U S in new tooling each year to manufacture the components that go into their new line of cars and trucks Spray forming offers great potential for reducing the cost and lead time for tooling by eliminating many of the machining grinding and polishing unit operations In addition spray forming provides a powerful means to control segregation of alloying elements during solidification and carbide formation and the ability to create beneficial metastable phases in many popular ferritic tool steels As a result relatively low temperature precipitation hardening heat treatment can be used to tailor properties such as hardness toughness thermal fatigue resistance and strength This paper describes the application of spray forming technology for producing H13 tooling for injection molding and die casting applications and the benefits of low temperature heat treatment RSP Tooling Rapid Solidification Process RSP Tooling is a spray forming technology tailored for producing molds and dies 2 4 The approach combines rapid solidification processing and net shape materials processing in a single step The general concept involves converting a mold design described by a CAD file to a tooling master using a suitable rapid prototyping RP technology such as stereolithography A pattern transfer is made to a castable ceramic typically alumina or fused silica Figure 1 This is followed by spray forming a thick deposit of tool steel or other alloy on the pattern to capture the desired shape surface texture and detail The resultant metal block is cooled to room temperature and separated from the pattern Typically the deposit s exterior walls are machined square allowing it to be used as an insert in a holding block such as a MUD frame 5 The overall turnaround time for tooling is about three days stating with a master Molds and dies produced in this way have been used for prototype and production runs in plastic injection molding and die casting Figure 1 RSP Tooling processing steps 3 An important benefit of RSP Tooling is that it allows molds and dies to be made early in the design cycle for a component True prototype parts can be manufactured to assess form fit and function using the same process planned for production If the part is qualified the tooling can be run in production as conventional tooling would Use of a digital database and RP technology allows design modifications to be easily made Experimental Procedure An alumina base ceramic Cotronics 780 6 was slurry cast using a silicone rubber master die or freeze cast using a stereolithography master After setting up ceramic patterns were demolded fired in a kiln and cooled to room temperature H13 tool steel was induction melted under a nitrogen atmosphere superheated about 100 C and pressure fed into a bench scale converging diverging spray nozzle designed and constructed in house An inert gas atmosphere within the spray apparatus minimized in flight oxidation of the atomized droplets as they deposited onto the tool pattern at a rate of about 200 kg h Gas to metal mass flow ratio was approximately 0 5 For tensile property and hardness evaluation the spray formed material was sectioned using a wire EDM and surface ground to remove a 0 05 mm thick heat affected zone Samples were heat treated in a furnace that was purged with nitrogen Each sample was coated with BN and placed in a sealed metal foil packet as a precautionary measure to prevent decarburization Artificially aged samples were soaked for 1 hour at temperatures ranging from 400 to 700 C and air cooled Conventionally heat treated H13 was austenitized at 1010 C for 30 min air quenched and double tempered 2 hr plus 2 hr at 538 C Microhardness was measured at room temperature using a Shimadzu Type M Vickers Hardness Tester by averaging ten microindentation readings Microstructure of the etched 3 nital tool steel was evaluated optically using an Olympus Model PME 3 metallograph and an Amray Model 1830 scanning electron microscope Phase composition was analyzed via energy dispersive spectroscopy EDS The size distribution of overspray powder was analyzed using a Microtrac Full Range Particle Analyzer after powder samples were sieved at 200 m to remove coarse flakes Sample density was evaluated by water displacement using Archimedes principle and a Mettler balance Model AE100 A quasi 1 D computer code developed at INEEL was used to evaluate multiphase flow behavior inside the nozzle and free jet regions The code s basic numerical technique solves the steady state gas flow field through an adaptive grid conservative variables approach and treats the droplet phase in a Lagrangian manner with full aerodynamic and energetic coupling between the droplets and transport gas The liquid metal injection system is coupled to the throat gas dynamics and effects of heat transfer and wall friction are included The code also includes a nonequilibrium solidification model that permits droplet undercooling and recalescence The code was used to map out the temperature and velocity profile of the gas and atomized droplets within the nozzle and free jet regions 4 Results and Discussion Spray forming is a robust rapid tooling technology that allows tool steel molds and dies to be produced in a straightforward manner Examples of die inserts are given in Figure 2 Each was spray formed using a ceramic pattern generated from a RP master Figure 2 Spray formed mold inserts a Ceramic pattern and H13 tool steel insert b P20 tool steel insert Particle and Gas Behavior Particle mass frequency and cumulative mass distribution plots for H13 tool steel sprays are given in Figure 3 The mass median diameter was determined to be 56 m by interpolation of size corresponding to 50 cumulative mass The area mean diameter and volume mean diameter were calculated to be 53 m and 139 m respectively Geometric standard deviation d d 84 d 16 is 1 8 where d 84 and d 16 are particle diameters corresponding to 84 and 16 cumulative mass in Figure 3 5 Figure 3 Cumulative mass and mass frequency plots of particles in H13 tool step sprays Figure 4 gives computational results for the multiphase velocity flow field Figure 4a and H13 tool steel solid fraction Figure 4b inside the nozzle and free jet regions Gas velocity increases until reaching the location of the shock front at which point it precipitously decreases eventually decaying exponentially outside the nozzle Small droplets are easily perturbed by the velocity field accelerating inside the nozzle and decelerating outside After reaching their terminal velocity larger droplets 150 m are less perturbed by the flow field due to their greater momentum It is well known that high particle cooling rates in the spray jet 10 3 10 6 K s and bulk deposit 1 100 K min are present during spray forming 7 Most of the particles in the spray have undergone recalescence resulting in a solid fraction of about 0 75 Calculated solid fraction profiles of small 30 m and large 150 m droplets with distance from the nozzle inlet are shown in Figure 4b Spray Formed Deposits This high heat extraction rate reduces erosion effects at the surface of the tool pattern This allows relatively soft castable ceramic pattern materials to be used that would not be satisfactory candidates for conventional metal casting processes With suitable processing conditions fine 6 Figure 4 Calculated particle and gas behavior in nozzle and free jet regions a Velocity profile b Solid fraction 7 surface detail can be successfully transferred from the pattern to spray formed mold Surface roughness at the molding surface is pattern dependent Slurry cast commercial ceramics yield a surface roughness of about 1 m Ra suitable for many molding applications Deposition of tool steel onto glass plates has yielded a specular surface finish of about 0 076 m Ra At the current state of development dimensional repeatability of spray formed molds starting with a common master is about 0 2 Chemistry The chemistry of H13 tool steel is designed to allow the material to withstand the temperature pressure abrasion and thermal cycling associated with demanding applications such as die casting It is the most popular die casting alloy worldwide and second most popular tool steel for plastic injection molding The steel has low carbon content 0 4 wt to promote toughness medium chromium content 5 wt to provide good resistance to high temperature softening 1 wt Si to improve high temperature oxidation resistance and small molybdenum and vanadium additions about 1 that form stable carbides to increase resistance to erosive wear 8 Composition analysis was performed on H13 tool steel before and after spray forming Results summarized in Table 1 indicate no significant variation in alloy additions Table 1 Composition of H13 tool steel Element C Mn Cr Mo V Si Fe Stock H13 0 41 0 39 5 15 1 41 0 9 1 06 Bal Spray Formed H13 0 41 0 38 5 10 1 42 0 9 1 08 Bal Microstructure The size shape type and distribution of carbides found in H13 tool steel is dictated by the processing method and heat treatment Normally the commercial steel is machined in the mill annealed condition and heat treated austenitized quenched tempered prior to use It is typically austenitized at about 1010 C quenched in air or oil and carefully tempered two or three times at 540 to 650 C to obtain the required combination of hardness thermal fatigue resistance and toughness Commercial forged ferritic tool steels cannot be precipitation hardened because after electroslag remelting at the steel mill ingots are cast that cool slowly and form coarse carbides In contrast rapid solidification of H13 tool steel causes alloying additions to remain largely in solution and to be more uniformly distributed in the matrix 9 11 Properties can be tailored by artificial aging or conventional heat treatment A benefit of artificial aging is that it bypasses the specific volume changes that occur during conventional heat treatment that can lead to tool distortion These specific volume changes occur as the matrix phase transforms from ferrite to austenite to tempered martensite and must be accounted for in the original mold design However they cannot always be reliably predicted Thin sections in the insert which may be desirable from a design and production standpoint are oftentimes not included as the material has a tendency to slump during austenitization or distort 8 during quenching Tool distortion is not observed during artificial aging of spray formed tool steels because there is no phase transformation An optical photomicrograph of spray formed H13 is shown in Figure 5 together with an SEM image in backscattered electron BSE mode Energy dispersive spectroscopic EDS composition analysis of some features in the photomicrographs is also given While exact quantitative data is not possible due to sampling volume limitations results suggest that grain boundaries are particularly rich in V Intragranular matrix regions are homogeneous and rich in Fe X ray diffraction analysis indicates that the matrix phase is primarily ferrite bainite with very little retained austenite and that the alloying elements are largely in solution Discrete intragranular carbides are relatively rare very small about 0 1 m and predominately vanadium rich MC carbides M 2 C carbides are not observed Element Si V Cr Mn Mo Fe Spot 1 wt 0 61 32 13 6 68 0 17 2 05 58 36 Spot 2 wt 1 59 0 79 5 35 0 28 2 28 89 72 Figure 5 Photomicrographs of as deposited H13 tool steel 3 nital etch a Optical photomicrograph b SEM image BSE mode near a grain boundary Table gives EDS composition of numbered features 9 Figure 6 illustrates the microstructure of spray formed H13 aged at 500 C for 1 hr During aging grain boundaries remain well defined perhaps coarsening slightly compared to as deposited H13 Figure 5 The most prominent change is the appearance of very fine 0 1 m diameter vanadium rich MC carbide precipitates The precipitates are uniformly distributed throughout the matrix and increase the hardness and wear resistance of the tool steel Increasing the soak temperature to 700 C results in prominent carbide coarsening the formation of M 7 C 3 and M 6 C carbides and a decrease in hardness The photomicrographs of Figure 7 illustrate the dramatic change in carbide size BSE imaging clearly differentiates Mo Cr rich carbides from V rich carbides shown as light and dark areas respectively in Figure 7 EDS analysis of these carbides is also given in Figure 7 Element Si V Cr Mn Mo Fe Spot 1 wt 0 06 13 80 7 20 2 64 2 44 73 86 Spot 2 wt 1 52 0 82 5 48 0 23 2 38 89 57 Figure 6 Photomicrographs of spray formed aged H13 tool steel 500 C soak for 1 hr 3 nital etch a Optical photomicrograph b SEM image BSE mode near a grain boundary Table gives EDS composition of numbered features 10 Element Si V Cr Mn Mo Fe Spot 1 wt 0 82 27 9 01 0 4 33 4 39 Spot 2 wt 0 5 30 25 70 0 55 55 13 45 Spot 3 wt 1 60 0 88 6 32 0 28 2 92 88 00 Figure 7 SEM Photomicrograph BSE mode of spray formed aged H13 tool steel showing adjacent V rich dark and Mo Cr rich light carbides 700 C soak for 1 2 hr 3 nital etch Table gives EDS composition of numbered features Material Properties Porosity in spray formed metals depends on processing conditions The average as deposited density of spray formed H13 was 98 99 of theoretical as measured by water displacement using Archimedes principle As deposited hardness was typically about 59 HRC harder than commercial forged and heat treated material 28 to 53 HRC depending on tempering temperature and significantly harder than annealed H13 200 HB The high hardness is attributable to lattice strain due to quenching stresses and supersaturation As shown in Figure 8 hardness can be varied over a wide range by artificial aging 59 HRC as deposited samples were given isochronal 1 hr soaks at 50 C increments from 400 to 700 C air cooled and evaluated for microhardness At 400 C a small decrease in hardness was observed presumably due to stress relieving As the soak temperature was further increased hardness rose to a peak hardness of approximately 62 HRC at 500 C Higher soak temperature resulted in a drop in hardness as carbide particles coarsened Peak age hardness in spray formed H13 tool steel is notably higher than that of commercial hardened material Normally commercial H13 dies used in die casting are tempered to about 40 to 45 HRC as a tradeoff since high hardness dies while desirable for wear resistance are prone to premature failure via thermal fatigue as the die s surface is rapidly cycled from 300 C to 700 C during aluminum production runs 11 Figure 8 Hardness of artificially aged spray formed H13 tool steel following one hour soaks at temperature Hardness range of conventionally heat treated H13 included for comparison As deposited spray formed material was also hardened following the conventional heat treatment cycle used with commercial material Samples of forged mill annealed commercial and spray formed materials were austenitized at 1010 C air quenched and double tempered 2 hr plus 2 hr at 538 C The microstructure in both cases was found to be tempered martensite with a few spheroidal particles of alloy carbide Hardness values for both materials were very nearly identical Table 2 gives the ultimate tensile strength and yield strength of spray formed cast and forged heat treated H13 tool steel measured at test temperatures of 22 and 550 C Values for spray formed H13 are given in the as deposited condition and following artificial aging and conventional heat treatments Values for the spray formed material are comparable to those of forged and are considerably higher than those of cast tool steel The spray formed material seems to retain its strength somewhat better than forged heat treated H13 at higher temperatures 12 Table 2 H13 tool steel mechanical properties Sample Heat Treatment Ultimate Tensile Strength MPa Yield Strength MPa Test Temperature C Spray formed as deposited 1061 951 22 Spray formed aged at 540 C 1964 1881 22 Spray formed aged at 540 C 1647 1475 550 Spray formed conventional heat treatment 1358 1158 22 Cast 600 22 Cast conventional heat treatment 882 22 Commercial forged heat treated 1799 1681 22 Commercial forged heat treated 1323 1247 550 austenitized at 1010 C double tempered 2hr 2hr at 590 C no yield at 0 2 offset Summary Spray forming is a robust rapid tooling technology that allows tool steel molds and di