機(jī)械類英語論文翻譯

1、.Influence of Hot Press Forming Techniques on Properties of Vehicle High Strength Steels( Scho ol of Automotive Engineering , State Key Laboratory of Structural Analysis for Industrial Equipment,Dalian University of Technology , Dalian 116024, Liaoning, China)Abstract: Based on the combination of ma

2、terials science and mechanicalengineering ,hotpress forming process of the vehicle high strength steels was analyzed. The hot forming processinclud -ed: heating alloy srapidly to austenite micr ostructures, stamping and cooling timely,maintaining pressur eand quenching . The results showed that most

3、 of austenite micr ostructure w as changed into uniform mar tensite by the hot press form ing while the samples were heatedat 900 。C and quenched. The optimal tensile strength and yield streng th were up to 1530 MPa and 1000 MPa, respectively, and the shape deformation reached about 23% . And spring

4、back defect did not happ -en in the samples.Key words: high streng th steel; lightw eight ; hot forming ; martensiteAs an effective economical energy measure, the lightw eight dev elo pment dir ection of automo -bile has become one of the most important research subjects in the automotive industry.

5、There are three major ways to achieve automobile light weight : optimizing vehicle frames and struc- tures; making vehicle bodyor f rame of new and alternativ ematerials to reduce the vehicle mass ( The high and ultra high strength steel can be used as alternative materials because of its thinner th

6、ickness) ; adopting advanced manufacturing techniques for the sake of automobile light wei- ght , such as thickness-gradient high strength steel (HSS) or metal based compound plates by con -tinuous pressing or hot press forming 1 . Although HSS has been applied in some domestic top grade vehicles, t

7、he key producing technologies have always been dominated by foreign compan- ies, such as Acelor Company, so as to raise the product cost obviously. By domestic self-designed hot press forming techniques and water-cooling mould, the automo bile HSS can be produced to subst itute foreign vehicle parts

8、.In general, with the enhancement of steel blank，s mechanical strength, its formability is worsened dramatically. It is difficult to apply the traditional cold stamping technolog y into the f ield of pressing HSS. Thus, the hot stamping technology of martensit icsteel blank is applied as a new techn

9、ology , which combines metal thermoplast ic forming metho d and water-cooling mould quenching principle. In this paper, boro n steel blank was formed and water-cooling mould was quenched simultane ously during the process of hot stamping . Comparedwith original automobile pearlite steel 2 , the auto

10、mobile HSS obtained by advanced hot press forming technique can reduce about 30% of the total vehicle mass and achieve complex g eomet ries, high security and mechanical st reng th. The r easo n is that austenite microst ructure with optimal plast icity and ductility can be obtained by hot press for

11、ming at high temperature 3- 5 , and the HSS with both excellent mechanical properties and light weight will be obtainedafter being formed and quenched 6- 8 . The application of hot-formed thinner HSS plates will becoman important measure to realize vehicle light weight.1 Experimental SetupIn order t

12、o form HSS at high temperature, and to avoid cracks and springback, the sam -ples need rapid heating and transform completely into stabl eaustenite microst ructure. And then, samples are pressed and cooled in self-made water-cooling mould.For the obtained HS -S sample, its shape-freezing character o

13、r no spring back defect is an obvious advantage, and most of microst ructure in the sample is martensite. The thickness of sample is 1.6 mm, and the main elements of HSS in this experiment are show n in Table 1.Table 1 Main elements of material in the experimen22MnB5CMnCrSiBPSAlMinimum0.2201.2000.11

14、00.0020.002-0.020Maximum0.2501.4000.2000.0050.0050.0200.0050.050Actual ex perimental procedure included: 1) set different heat t reatment temper atures in ther ange of750 to 1 000; 2) put the sample into the heat treated furnace to be heated for 4 min at a certain temperature; 3) remove it by mechan

15、ical hand and put it into the hot forming moulds to be pressed quickly ;4) simultaneously, it was water-cooled at about 30/s in the mound. The mechanical properties of sample were analyzed by tensile test system and the microstructure appear ance was analyzed by metal lographic analysis device.The s

16、hape and size of test sample are show n in Fig. 1.Fig 1 The shape and size of specimen2 Results and DiscussionMechanical propert ies of HSS ( boron steels)with different thicknesses ( 1.0mm, 1.6mm, 2.0mm,2.5 mm, 3.0 mm and 4.0 mm, respectively) were checked (GBT 16865-1997 was consulted, and samples

17、 were selected along 0, 45 and 90 rolling direction respec -tively ) . The unidirectional tensile tests (based on the metal tensile test ing standard of GBT228-2002 ) were finished. Compared with USIBOR1500, the values of basic mechanical properties for HSS w ith dif ferent thicknesses in the experi

18、ment are shown in Fig 2. Fig 2 shows that after water-cooling quenching , the tensile strength and yield strength of samples ( except the one w ith thickness of 4.0 mm )reached 1 500 MPa and 1 000 MPa, respect ively. The values of the strength were twice bet ter than those of samples before quenchin

19、g , and nearly the same to those of the plates of thickness 1.75 mm from Acelor Company ( USIBOR1500 shown in Fig 1) .Fig2 Tensile and yield strength of high strength steels with different thicknesses before and after quench ingGenerally , hot press forming of samples is operated above transition te

20、mperature of martensite micro structure. The heating temperature in this experiment was in the range of 750 to 1000 because it took 3 s or so for the samples to be delivered in the air. And then, based on analyzing tensile strengths Rm of samples after hot-forming at different temperatur -es and que

21、nching , the optimal temperature can be found. It is shown in Fig3. Fig3 Curve of tensile strength vs preheating temperatureFrom Fig 3, it is obvious that the value of tensile strength Rm only reaches 900 MPa at 750 ; the optimal value is 1530 MPa at 900 , and the value will fall as temperature is s

22、et above 900 . Based on analy zing microstructure and Fe-Fe3 C phase diagram, samples lay in the transition region of ferrite austenite microstr ucture coexistence at 750 . At this moment , austenite has appeared in microstructure of samples, and it can be transformed into martensite microstructure

23、through water-cooling. So the mechanical properties, such as tensile strength and yield strength, will be improved. That is to say ,tensile strength of samples is a little hig her than that of original ones ( Rm is 600 MPa or so) . The content of austenite becomes larger as temperature is raised,and

24、 the tensile str ength will be improved gradually .As far as 22MnB5 steel is concerned, the austenitizing temperature is about 880 . As Fig3 shows, if samples are heated rapidly to 900 and air cooled for 3, austenite microstr uctures are obtained completely . Then samples are hot formed and water-co

25、oling quenched, the fraction of martensite microstructure in samples is more than 95% , so the curve shows a peak. How ever, as temperature exceeds 900 , because superheat degree is too large, microg rains grow so large that the tensile strength will decrease. Thus high tem- perature austenite micro

26、structure (obtained as samples w ere heated rapidly) and grain refinement are the main factors to determine the mechanical properties of high strength steel -s. In this paper, different from that in the lab,the interact ion mechanisms of molding and w ater-cooling system on samples produced in the p

27、roduction line can objectively show the manufacturing properties and microst ructure character of products in mass.A s far as the samples are concerned, A is the initial and untreated sample; B is the sample which was heated at 900 for 4 min; C is the sample after heat treatment and water-coo ling q

28、uenching. The deformation of A, B and C are 32% , 24% and 6% or so, respectively . Generally , A is composed of main pearlite and a small amount of ferrite, thetoughness of which is better than martensite, so its deformation is relatively better. B is com -posed with the high-temperature transitiona

29、l microstructure of austenite, whose toughness is also better than martensite, and deformation is larger than the latter. C is composed of over 95% martensite and little austensite. Owing to its higher strength, toughness and plasticity of martensite are lower, that is to say , deformation of C is t

30、he lowest In Fig 4, when the sample was heated for 4 min and stretched at 900 , stress-strain curve and testforce displacement curve were obtained respect ively.From Fig4 ( a) , after being heated up to 900,the microst ructure of sample has been completely turned into austenite. T he value in the el

31、astic deformation stage of curve w ill tend towards the yield point , following the axial test force gradually being increased. That is to say, the obvious plastic deformation of sample will beg in after the yield point .When it is continuously stretched till the peak point of curve, the necking of

32、sample will occur. Passing the peak, the st ress-strain relat ionship will become more complex . From Fig 4 ( b) , after the corresponding peak, the test force will be reduced, along with the decreasing cross-sectional area of sample till the f racture. It can be seen that the appropriate toughness

33、and plastic deformation proper ties of austenitizing sample at 900 will help HSS be hot- formed to complicate vehicle parts. It is an effective measure to form HSS with room-temperature martensite microstructure character, and it is a theoretical basis to design the hot-forming process for HSS in th

34、e article.The vehicle hot forming parts and the original cold forming parts are practically contrasted. There areobvious differences both in the springback defect and in the formability, as shown in Fig5.From Fig5, it shows that the hot-forming parts havehig her accuracy, almost no shape distortion,

35、 and no springback defect . But the cold-forming parts will exhibit deformation defects, crimping,large spring back and twisted grooves obviously,which can destroy the yield of products seriouslyw hich can destroy the yield of products seriously .Therefore, instead of tradit ional cold forming , the

36、 vehicle-high strength steels which are produced by hot forming have become an inevitable trend. In addition, the compositions of samples are shown inTable 1, based on not only the contribution for formability and microst ructure, but also the cost .For example, component boron as a component of sam

37、ple can reduce the energy-gradient on the grain boundary because it is easily adsorbed on grain boundary to fill the defect of lower energy. Whileaustenitizing temperature is decreased by water-cooling system, -phase ferrite is easily to be nucleated on the grain boundaries. But the nucleation and g

38、rowth of ferrite and bainite will become slower because of the low erenergy gradient on the grain boundaries, and are beneficial to make austenite stable; if the co ntent of boronor processing parameters are unsuitable, component boron would be precipitated to super saturation on the grain boundarie

39、s and become the new nucleus of precipitating phase which makes ener gy gradient larger, causing the harden ability of samples to fall.( a) Stressst rain curve; ( b) Test force displacement curveFig 4 Curves of stress-strain and test force displacement for stretching testIn the production line, the

40、precipitation and growth of mixed phase will be prohibited effectively by controlling temperature and heating rate. The sample is heated to 900 and held for 4 min. The microstructure appearance of sample after quenching at cooling rate of no less than 30/ s is show n in Fig 6. Fig5 Picture of hot fo

41、rming and cold forming vehicle partsIn Fig6 ( a) , the main micro structur e of initial sample, w hich has not been hot formed and water-cooling quenched, is composed offerrite, pearlite and a small amount of carbide. Its tensile strength Rm and yield strength are only 653MPa and 500MPa, respectivel

42、y . Fig6 ( b) shows that most microstructure of sample after quenching is strip-shapemartensite, the content of which is over 95% , and there are no cracks and other stress defects. The reason is that the sample was evenly heated and water-cooled during the whole process; based on “C”curve, even and

43、 close-row lath martensite microsructure obtained is also due to the optimal water-cooling rate, so the content of residual phase is very little; in addition, the complete close-row microstructure shows that residual stress ( including thermal stress and phase transformation stress, etc. )has been r

44、eleased completely, and there is no microgap in the micrograins so as to benef it sample for higher security and better mechanical propert ies.T he domestic research of vehicle HSS is mostly limited to do in the lab, but advanced automated manufacturing technologies are difficult to be realized in t

45、he lab. In this paper ,the properties targets of HSS produced by practical production line are satisfactory, and the technical process also meets the demands of mass production(a) Original HSS microstructure before hot forming and quenching; (b) Obtained HSS microstructure after hot forming and quen

46、ching.Fig6 Microstructure appearance of HSS sample bef ore and after hot forming and quenching3 Conclusions 1) In the production line, as HSS is heated rapidly to 900 and held for 4 min, the tensile strength can reach the optimal value of 1530 MPa.If temperature is too low , austenite transformation

47、 will be incomplete; on the contrary , if temperature is too high, micrograin will grow too large. Both of them will reduce the tensile strength.2) T hanks to the appropriate toughness and plastic deformation properties of austenitizing HSS at high temperature, 22MnB5 steels ( HSS) can be favorably

48、hot formed into complex and accurate automotive parts.3) T he optimal water-cooling rate during quenching can make HSS achieve the ideal microstructure of more than 95% martensite and a very small amount of residual austenite, and help stress-relieving procedure accomplish effectively. It is also th

49、e guarantee for HSS parts to possess high strength and no defects, such as cracks and crimping.References: 1 Schiel G, Pos schn T , Heller T , etal. Manufacturing a Roof Frame From Ultra High Strength Steel Materials by Hot Stamping C IDDRG In ternational Deep Drawing Research Group 2004 Conference.

50、 Sindelfingen: s. n. , 2004: 158. 2 TANG Zhiyong, J IANG Haitao, TANG Di, etal. Study on the Continuous Cooling Transformati on of Austenite of 27MnC rB5 Steels J . Hot Working Technology, 2007, 36( 20) : 41. 3 FAN Junf eng, CHEN Ming. A Study on the Road of Vehicle Lightw eight in Chin a J .Casting

51、2006, 55( 10) : 995 ( in Chinese) . 4 CHEN He-qin g, PENG C hengyun, WEI Liangqing. High Strength Steels and Applicati on of Them to Vehicle Manufacturing J . Mould and Die Project, 2007 ( 8) : 88 ( in Chinese) . 5 LIN Jianping, WANG Liying, TIAN Haob in, etal. Research and Devel opment of the Hot P

52、ress Form -ing of Ultra High Strength Steel J . Metal Casting Forgin g Welding Technology, 2008, 37( 21) : 140 ( in Chinese) . 6 XING Zhongwen, BAO Jun, YANG Yuying, etal. Hot Press Forming Experiment al Research on the Quenchenable Boron St eel J . Materials Science and Technology, 2008, 16( 2) : 1

53、72. 7 Marion Merklein , Jrg en Lecher, Vera Gdel, et al. Mech anical Properties and Plastic Anisotropy of the Quenchenable High Strength Steel 22MnB5 at Elevated Temperatures J . Key Engineering Materials, 2007, 344: 79. 8 Geigera M, Merkleinb M, H off C. Basic Investigations on the Hot Stamping Ste

54、el 22MnB5 J . Advanced Materials Research, 2005, 6( 8) : 795.熱壓成形技術(shù)對汽車高強(qiáng)度鋼性能影響常英，孟召喚，梁穎，李曉東，馬寧，胡平（學(xué)院汽車工程國家重點(diǎn)實(shí)驗(yàn)室，工業(yè)裝備結(jié)構(gòu)分析，大連理工大學(xué)，遼寧，大連，116024）摘要：基于材料科學(xué)和機(jī)械工程的結(jié)合上，車高強(qiáng)度鋼熱沖壓成型過程進(jìn)行了分析。熱成型工藝包括：快速加熱合金，奧氏體微觀結(jié)構(gòu)，沖壓和及時(shí)冷卻，保持壓力和淬火。結(jié)果表明，對樣品進(jìn)行淬火的熱壓成形，加熱至900時(shí)，大部分奧氏體微觀結(jié)構(gòu)改變成均勻的馬氏體。最佳的拉伸強(qiáng)度和屈服強(qiáng)度分別為1530 MPa和1000MPa的，均達(dá)到2

55、3左右的形狀變形。樣品沒有發(fā)生過回彈缺陷。關(guān)鍵詞：高強(qiáng)度鋼；重量輕；熱成型；馬氏體0 引言作為一種有效的經(jīng)濟(jì)的能源措施，輕巧的汽車發(fā)展方向，已成為汽車行業(yè)最重要的研究課題之一。實(shí)現(xiàn)汽車輕量化的主要途徑有三個(gè)：優(yōu)化汽車框架和結(jié)構(gòu)，使車輛的車身或者車架的，新的和替代材料，降低整車質(zhì)量（高和超高強(qiáng)度鋼，可作為替代材料，因?yàn)樗暮穸雀?，），汽車輕量化，如厚度梯度高強(qiáng)度鋼（HSS）或金屬系化合物板通過連續(xù)沖壓或熱壓成形1為了采用先進(jìn)的制造技術(shù)。HSS已經(jīng)應(yīng)用在國內(nèi)一些高檔車，關(guān)鍵生產(chǎn)技術(shù)一直占主導(dǎo)地位的外國公司，如Acelor公司，從而顯著提高了產(chǎn)品成本。由國內(nèi)自行設(shè)計(jì)的熱壓成型技術(shù)和水冷卻模具，汽車

56、HSS可以生產(chǎn)替代國外汽車零部件。在一般情況下，隨著鋼質(zhì)坯件的機(jī)械強(qiáng)度的增強(qiáng)，其可塑性急劇惡化。這是很難適用于傳統(tǒng)的冷沖壓技術(shù)進(jìn)入該領(lǐng)域取代HSS。同時(shí)，填補(bǔ)了馬氏體鋼應(yīng)用空白，熱沖壓技術(shù)作為一項(xiàng)新技術(shù)，它結(jié)合了金屬熱塑性成型法和水冷卻模具淬火原則。在本文中，形成硼鋼空白和水冷卻用模具驟冷的過程期間同時(shí)燙印。相對于原汽車珠光體鋼2，汽車HSS通過以下方式獲得先進(jìn)的熱壓成形技術(shù)可以減少車輛的總質(zhì)量的30左右，實(shí)現(xiàn)復(fù)雜的幾何形狀，高安全性和機(jī)械強(qiáng)度。其原因是最佳的塑性和延展性的奧氏體顯微組織可以通過高溫下3 - 5熱壓成形方式獲得，同時(shí)形成后和驟冷的6 - 8條件將得到具有優(yōu)異機(jī)械性能、重量輕的H

57、SS將。為實(shí)現(xiàn)車輛的重量輕，熱成型更薄的HSS板的應(yīng)用將成為一個(gè)重要的措施。1實(shí)驗(yàn)裝置另外，為了在高溫下形成高速鋼，以避免裂紋和回彈，樣品需要快速加熱和完全變換成穩(wěn)定的奧氏體組織。然后，樣品被壓在自制的水冷卻模具中冷卻，對于得到的HSS樣本，其形狀凍結(jié)字符或沒有回彈缺陷是一個(gè)明顯的優(yōu)點(diǎn)，并且大部分樣品中的顯微組織為馬氏體。樣品的厚度是1.6毫米，在HSS這個(gè)實(shí)驗(yàn)中的主要元素，示于表1。表1的實(shí)驗(yàn)技術(shù)中的材料的主要要素22MnB5CMnCrSiBPSAl最低限度0.2201.2000.1100.0020.002-0.020最高限度0.2501.4000.2000.0050.0050.0200.0

58、050.050實(shí)際實(shí)驗(yàn)步驟包括：1）設(shè)置不同的熱處理溫度的范圍為750至1 000；2）把熱處理過的樣品放入爐中，在一定的溫度下加熱4分鐘；3）刪除它由機(jī)械手并把它變成熱成形模具，快速按下；4）同時(shí)，在約30/ s的冷卻水在土堆，通過拉伸試驗(yàn)系統(tǒng)進(jìn)行分析的樣品的機(jī)械性能和由金屬金相圖片分析裝置分析的顯微組織的外觀。試驗(yàn)樣品的形狀和尺寸示于圖1。2結(jié)果與討論硼鋼（HSS）的機(jī)械性能不同厚度（1.0毫米，1.6毫米，2.0毫米，2.5毫米，3.0毫米和4.0毫米，分別）進(jìn)行了檢查（GBT16865-1997征求意見，樣本選取沿0，45和90軋制方向分別）。單向拉伸試驗(yàn)（金屬拉伸試驗(yàn)的標(biāo)準(zhǔn)GBT228-2002）的基礎(chǔ)上被完成。相比與USIBOR1500，HSS具有不同厚度的實(shí)驗(yàn)中基本力學(xué)性質(zhì)的值如圖2所示。單位：mm圖1形狀和尺寸試樣圖2示出了樣品（除了用厚度為4.0毫米的一個(gè)）的拉伸強(qiáng)度和屈服強(qiáng)度，水冷淬火后，分別達(dá)到1500 MPa和1 000兆帕。淬火前的強(qiáng)度的值的兩倍優(yōu)于那些樣本，和幾乎相同的那些板的厚度