C5191磷青铜机械性能参数

磷青铜-黄铜等材料性能规格磷青铜(Phosphor Bronze) 特性及规格一览表：(1)化学成份(Chemical Composition)(2)物理特性(Physical Properties)(3)机械性质(Mechanical Properties)固溶热处理, 冷加工至1/8 硬(1/8H)；固溶热处理, 冷加工至硬态(H)；沉淀硬化(AT)；1/4 硬和沉淀热处理(1/4HT)；半硬和沉淀热处理(1/2HT)O：退火（软）状态；H：加工硬状态；EH：特硬状态；SH：抗拉强度最大的加工制品；Mechanical Properties (continuous)SH C5191R-SH> 0.2> 75> 5230~270C5212O CC5210R-O> 0.2> 35> 45-H/4C5210R-H/4> 0.240~52> 40120~150 H/2C5210R-H/2> 0.250~60> 30150~170 3/4H C5210R-3/4H> 0.252~62> 20170~190 H C5210R-H> 0.260~72> 12190~210 EH C5210R-EH> 0.270~80> 8210~230 SH C5210R-SH> 0.2> 75> 5230~270黄铜(Brass) 特性及规格一览表：(1)化学成份(Chemical Composition)合金编号化学成份(wt.%)Material Designation Cu Zn Fe PbJIS C2600C2680C280168.5~71.564.0~68.559.0~63.0Rem.Rem.Rem.0.05(max)0.05(max)0.05(max)0.07(max)0.15(max)0.30(max)(2)物理特性(Physical Properties)合金编号(Alloy No. ) 密度(Density)g/cm3弹性系数(Modulus ofElasticity)(Young’s Modulus)GPa热膨胀系数(Coefficient of ThermalExpansion at 20 o C to 300o C)m/m．K热传导系数(ThermalConductivityat 20 o C)W/m．K导电率(ElectricalConductivity at 20o C)%IACS(3)机械性质(Mechanical Properties)C194合金(HSM Copper)特性及规格一览表：(1)化学成份(Chemical Composition)合金编号化学成份(wt.%)Material Designation Cu Fe P Zn PbJIS C194Rem. 2.10~2.600.015~0.150.05~0.20<0.03 (2)物理特性(Physical Properties)合金编号(Alloy No. ) 密度(Density)g/cm3弹性系数(Modulus ofElasticity)(Young’sModulus)GPa热膨胀系数(Coefficient of ThermalExpansion at 20 o C to300 o C)m/m．K热传导系数(ThermalConductivityat 20 o C)W/m．K导电率(ElectricalConductivity at20o C)%IACSC1948.8312116.326265 (3)机械性质(Mechanical Properties)合金编号质别Temper符号Symbol抗拉试验Tensile test硬度试验Hardness testAlloyNo.厚度Thickness(mm)抗拉强度Tensilestrength(kgf/mm2)延伸率(50mm)Elongation(in 2”)(%)HvThickness>0.15mmC194O C194R-O> 0.231~38> 2590~115 H/2C194R-H/2> 0.237~44> 6115~135 H C194R-H> 0.242~49> 3125~145 EH C194R-EH> 0.247~51> 2135~150 SH C194R-SH> 0.249~53-140~155 ESH C194R-ESH> 0.251~56-145~160红铜(Copper) 特性及规格一览表：(1)化学成份(Chemical Composition)合金编号化学成份(wt.%)Material Designation Cu PJIS C1100(ETP)C1200(DLP)C1220(DHP)99.9(min)99.9(min)99.9(min)-0.004~0.0120.015~0.040(2)物理特性(Physical Properties)(3)机械性质(Mechanical Properties)磷青铜(Phosphor Bronze)合金各规格对照表规格名称SPEC 合金编号Alloy No.化学成分Chemical Composition (wt.%)规格编号Spec no.Cu Sn P Fe Ni Pb Zn OthersISO CuSn 4Rem.3.5~4.50.01~0.40≦0.1≦0.3≦0.05≦0.3----427 CuSn 5 4.5~5.5CuSn 6 5.5~7.5CuSn 87.5~9.0CNS C5101Rem.3.0~5.50.03~0.35----------------Cu＋Sn＋P≧99.59503H3112 C5191 5.5~7.0C52127.0~9.0JIS C5111Rem.3.5~4.50.03~0.35----------------Cu＋Sn＋P≧99.5H3110 C5102 4.5~5.5C5191 5.5~7.0C52127.0~9.0C52107.0~9.0≦0.1----≦0.05≦0.2Cu＋Sn＋P≧99.7H3130ASTM C51100Rem.3.5~4.90.03~0.35≦0.1----≦0.05≦0.3----B103 C51000 4.2~5.8C51900 5.0~7.0C521007.0~9.0≦0.2DIN CuSn 4Rem.3.5~4.50.01~0.35≦0.1≦0.3≦0.05≦0.3≦0.217662 CuSn 6 5.5~7.5CuSn 87.5~8.5BS PB101Rem.3.5~4.50.02~0.40--------≦0.02≦0.3----2870 PB102 4.5~5.5PB103 5.5~7.5铜合金板材厚度公差(Thickness tolerances for strip):红铜(C1100、C1200、C1220)黄铜(C2600、C2680、C2801)磷青铜(C2600、C2680、C2801)特殊铜合金(C194)over 0.70 mm to 0.90 mm incl.±0.035 mm±0.060 mm±0.015 mmover 0.90 mm to 1.20 mm incl.±0.040 mm±0.070 mm±0.020 mmover 1.20 mm to 1.50 mm incl.±0.045 mm±0.080 mm±0.025 mmover 1.50 mm to 2.00 mm incl.±0.050 mm±0.090 mm±0.025 mm 铜合金板材宽度公差(Width tolerances for strip):宽度Width厚度Thickness 厚度公差ToleranceJIS Standard (H3100)S&T≦100 mm≦200 mm≦100 mm≦200 mm0.10 ~ 0.55 mm.±0.10 mm±0.20 mm±0.05 mm±0.10 mm0.55 ~ 2.00mm.±0.20 mm±0.30 mm±0.10 mm±0.20 mm 铜合金板材蛇弯度公差(Permissible max. value on camber):宽度Width公差Tolerance (per 1000 mm)over 6 mm to 9 mm inc9 mm max.over 9 mm to 13 mm incl. 6 mm max.over 13 mm to 25 mm incl. 4 mm max.over 25 mm to 50 mm incl. 3 mm max.over 50 mm to 100 mm incl. 2 mm max.over 100 mm 1 mm max.* Dimensional tolerances shall be in accordance with JIS H3100。

磷青铜-黄铜等材料性能规格磷青铜 (Phosphor Bronze) 特性及规格一览表：(1)化学成份 (Chemical Composition)(2)物理特性(Physical Properties)热膨胀系数(Coefficient of ThermalExpansion at 20 oC to 300 oC)m/m ．K 热传导系数(ThermalConductivityat 20 W/m(3)机械性质(Mechanical Properties)固溶热处理 , 冷加工至 1/8 硬 (1/8H)；固溶热处理 , 冷加工至硬态 (H)；沉淀硬化 (AT)；1/4 硬和沉淀热处理 (1/4HT)；半硬和沉淀热处理 (1/2HT)O ：退火（软）状态；H ：加工硬状态； EH ：特硬状态；SH ：抗拉强度最大的加工制品；Mechanical Properties (continuous)黄铜 (Brass) 特性及规格一览表：(1)化学成份 (Chemical Composition)(2)物理特性(Physical Properties)热膨胀系数(Coefficient of Thermal Expansion at 20 oC to 300oC) m/m ．K热传导系数(ThermalConductivity at 20 W/m(3)机械性质(Mechanical Properties)C194合金(HSM Copper)特性及规格一览表：(1)化学成份(Chemical Composition)(2)物理特性(Physical Properties)热膨胀系数(Coefficient of ThermalExpansion at 20 o C to 300 o C)m/m．K 热传导系数(Thermal Conductivity at 20W/m(3)机械性质(Mechanical Properties)红铜 (Copper) 特性及规格一览表：(1)化学成份(Chemical Composition)(2)物理特性(Physical Properties)热膨胀系数(Coefficient of Thermal Expansion at 20 oC to 300oC) m/m ．K热传导系数(ThermalConductivity at 20 W/m(3)机械性质(Mechanical Properties)磷青铜(Phosphor Bronze)合金各规格对照表铜合金板材厚度公差 (Thickness tolerances for strip): 红铜 (C1100、C1200、C1220)黄铜 (C2600、C2680、C2801)磷青铜 (C2600、C2680、C2801)特殊铜合金 (C194)铜合金板材宽度公差 (Width tolerances for strip):铜合金板材蛇弯度公差 (Permissible max. value on camber):* Dimensional tolerances shall be in accordance with JIS H3100。

磷青銅 (Phosphor Bronze) 特性及規格一覽表(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)Mechanical Properties (continuous)黃銅 (Brass) 特性及規格一覽表(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)C194合金(HSM Copper)特性及規格一覽表(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)紅銅 (Copper) 特性及規格一覽表(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)磷青銅(Phosphor Bronze)合金各規格對照表銅合金板材厚度公差(Thickness tolerances for strip) 銅合金板材寬度公差(Width tolerances for strip):紅銅(C1100、C1200、C1220)黃銅(C2600、C2680、C2801)磷青銅(C2600、C2680、C2801)特殊銅合金(C194)銅合金板材蛇彎度公差(Permissible max. value on camber):* Dimensional tolerances shall be in accordance with JIS H3100。

磷青銅(Phosphor Bronze) 特性及規格一覽表：(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)Mechanical Properties (continuous)黃銅(Brass) 特性及規格一覽表：(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)C194合金(HSM Copper)特性及規格一覽表：(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)紅銅(Copper) 特性及規格一覽表：(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(3)機械性質(Mechanical Properties)磷青銅(Phosphor Bronze)合金各規格對照表銅合金板材厚度公差(Thickness tolerances for strip):紅銅(C1100、C1200、C1220)黃銅(C2600、C2680、C2801)磷青銅(C2600、C2680、C2801)特殊銅合金(C194)銅合金板材寬度公差(Width tolerances for strip):銅合金板材蛇彎度公差(Permissible max. value on camber):* Dimensional tolerances shall be in accordance with JIS H3100。

C51900锡磷青铜板，棒管的化学成分和力学性能-绿兴金属描述C51900锡磷青铜板、铜管化学成分和力学性能绿兴金属生产推荐。

相关性能和了解更多加工性能可以百度绿兴金属找到我们。

C51900锡磷青铜有高的强度、弹性、耐磨性和抗磁性，在热态和冷态下压力加工性良好，对电火花有较高的抗燃性,可焊接和纤焊，可切削性良好，在大气、淡水中耐蚀。

C51900锡磷青铜板特性及适用范围：C51900锡磷青铜有高的强度、弹性、耐磨性和抗磁性，在热态和冷态下压力加工性良好，对电火花有较高的抗燃性,可焊接和纤焊，可切削性良好，在大气、淡水中耐蚀。

C51900用于制作弹簧和导电性好的弹簧接触片，精密仪器中的耐磨零件和抗磁零件，如齿轮、电刷盒、振动片、接触器等。

以锡为主要合金元素的青铜。

含锡量一般在3～14%之间，主要用于制作弹性元件和耐磨零件。

变形锡青铜的含锡量不超过8%，有时还添加磷、铅、锌等元素。

磷是良好的脱氧剂，还能改善流动性和耐磨性。

锡青铜中加铅可改善可切削性和耐磨性，加锌可改善铸造性能。

这种合金具有较高的力学性能、减磨性能和耐蚀性，易切削加工，钎焊和焊接性能好，收缩系数小，无磁性。

可用线材火焰喷涂和电弧喷涂制备青铜衬套、轴套、抗磁元件等涂层。

尺寸规格有Ф1.6mm、Ф2.3mm。

具有较高的强度、耐蚀性和优良的铸造性能，长期以来广泛应用于各工业部门中C51900锡磷青铜板化学成份：铜Cu ：余量锡Sn ：6.0～7.0铅Pb：≤0.02磷P：0.10～0.25铝Al：≤0.002铁Fe：≤0.05硅Si ：≤0.002锑Sb ：≤0.002铋Bi：≤0.002注：≤0.1(杂质)C51900锡磷青铜板力学性能：抗拉强度σb (MPa)：≥470伸长率δ5 (%)：≥13注：棒材的纵向室温拉伸力学性能试样尺寸：直径或对边距离5～12热处理规范：热加工温度750～770℃;退火温度600～650℃。

C51900锡磷青铜板特性锡青铜除了含有3%～14%锡，此外还常常加入磷、锌、铅等元素。

磷青銅材料性能規格磷青銅(Phosphor Bronze) 特性及規格一覽表：(1)化學成份(Chemical Composition)(2)物理特性(Physical Properties)(Young’s Modulus)熱膨脹係數(Coefficient of ThermalExpansion at 20 o C to300 o C)m/m．K熱傳導係數(ThermalConductivityat 20W/m(3)機械性質(Mechanical Properties)固溶熱處理, 冷加工至1/8 硬(1/8H)；固溶熱處理, 冷加工至硬態(H)；沉澱硬化(AT)；1/4 硬和沉澱熱處理(1/4HT)；半硬和沉澱熱處理(1/2HT)O：退火（軟）狀態；H：加工硬狀態；EH：特硬狀態；SH：抗拉強度最大的加工製品；磷青銅(Phosphor Bronze)合金各規格對照表銅合金板材厚度公差(Thickness tolerances for strip):磷青銅(C2600、C2680、C2801)銅合金板材寬度公差(Width tolerances for strip):銅合金板材蛇彎度公差(Permissible max. value on camber):* Dimensional tolerances shall be in accordance with JIS H3100合金種類含錫丹銅磷青銅C4250C4250M C5050C5111C5102C5191C5210化性成份(%)銅:87~90.錫:1.5~3.0鋅:餘量銅:86~88錫:2.5~4.鋅:餘量銅:餘量.錫:1.0~1.7磷:0.004~0.01銅:餘量.錫:3.5~4.9磷:0.11~0.13銅:餘量.錫:4.5~5.5磷:0.11~0.13銅:餘量.錫:5.5~7.0磷:0.11~0.13銅:餘量.錫:7.0~9.0磷:0.15~0.17比重(gm/cm3)8.7 88.788.898.868.868.838.80熱膨脹係數(10-6/℃)18.518.517.817.817.81818.2熱傳導係數(Cal/cm2/cm/sec/℃)0.290.250.490.200.170.160.15導電率(%IACS, 20℃)≧26≧24≧45≧20≧20≧13≧12抗張強度(N/mm 2)燒燉軟化295~380≧245≧245≧295≧300310~395--1/4H340~405340~405--345~440370~470395~490--1/2H390~475390~475360~425410~510470~570490~590470~610 3/4H430~510430~510----------H480~565480~565390~470490~590570~670525~670585~710 EH525~605525~605440~510≧570≧615≧670635~735 SH580~650580~650≧490------≧725 ESH≧635≧635----------伸長率(%)燒燉軟化≧35≧40≧25≧38≧40≧42--1/4H≧25≧30--≧25≧28≧35--1/2H≧15≧20≧15≧12≧15≧20≧27 3/4H≧10≧15----------H≧5≧10≧5≧7≧7≧10≧20 EH----≧2≧3≧4≧5≧11 SH------------≧9。

Trans.Nonferrous Met.Soc.China31(2021)692−702Microstructural characterization of blanked surface of C5191phosphor bronze sheet under ultra-high-speed blankingDao-chun HU1,2,Ming-he CHEN2,Lei WANG2,3,Hong-jun WANG11.Engineering Technology Training Center,Nanjing Vocational University of Industry Technology,Nanjing210023,China;2.Jiangsu Key Laboratory of Precision and Micro-Manufacturing Technology,Nanjing University of Aeronautics and Astronautics,Nanjing210016,China;3.School of Mechanical Engineering,Nanjing Vocational University of Industry Technology,Nanjing210023,ChinaReceived3March2020;accepted10November2020Abstract:The deformation mechanism of C5191phosphor bronze sheet under ultra-high-speed blanking was investigated.By virtue of a DOBBY-OMEGA F1ultra-high-speed press,the ultra-high-speed blanking test was conducted on C5191phosphor bronze sheets with a thickness of0.12mm at3000strokes per minute.The microstructures of the blanked edges were characterized and analyzed separately by electron back-scatter diffraction (EBSD)and transmission electron microscopy(TEM).The results show that grains in the blanked edges are stretched along the blanking direction.Strong{001}〈100〉cube textures(maximum pole densities of9and12,respectively)and secondarily strong{011}011〈〉textures(maximum pole densities of4and7,respectively)are formed in local zones. Additionally,deformation twins are found in the shear zone of the blanked edges which are rotated and coarsened due to the blanking-induced extrusion and local thermal effect which can further form into sub-grains with clear and high-angle boundaries.The C5191phosphor bronze sheet is subjected to adiabatic shear during ultra-high-speed blanking,accompanied with dynamic recrystallization.Key words:C5191phosphor bronze;ultra-high-speed blanking;blanked surface;adiabatic shear;dynamic recrystallization1IntroductionMetal workpieces in information technology (IT)devices including connector terminals in computer,communication and consumer electronics (3C)products,lead frames of integrated circuits, aerospace electrical connectors,and connectors for high-speed data transmission of car on internet in the era of big data.These workpieces are all characterized by ultra-thin thickness(lower than 500μm),complex shapes,small sizes,high requirements on size and location precision(nearly micron-order)and high demand[1].Products are required to integrate an increasingly number of functions and show high performance.They are becoming smaller,while exhibit more elaborated appearance and have a more frequent upgrading rate due to very high demand in the market.The workpieces have massive increasing demands on low-cost and good quality,which generally requires manufacturing in large quantities using high-speed and precision progressive stamping technology.Blanking is considered as the most fundamental and frequently used process in high-speed and precision progressive stamping.It can not only be used to manufacture blanks in the early period for the subsequent processes such asCorresponding author:Ming-he CHEN;Tel:+86-25-84892508;E-mail:******************.cn DOI:10.1016/S1003-6326(21)65530-91003-6326/©2021The Nonferrous Metals Society of China.Published by Elsevier Ltd&Science PressDao-chun HU,et al/Trans.Nonferrous Met.Soc.China31(2021)692−702693bending and drawing,but also be used as the finalprocess to directly shape and manufacture preciseblanked parts.The blanked edges determine the quality of blanked parts.During the whole processof blanking,plastic deformation,fracture andseparation of metal materials are only found in alocalized zone around the cutting edges.The cuttingedges were subjected to huge vertical and lateralpressures,and those high pressures will produce a large quantity of friction heat.Moreover,the blanking process continuously lasts for a long time, which results significant local temperature-rise and softening effect[2,3].Additionally,the strain-rate hardening and strain hardening of materials under a high rate and large strain make the fracture mechanism of high-speed precise blanking more complex.Also,due to the constraints of service conditions(such as low fracture zones,short response time and difficulty in on-line detection),it is hard to quantitatively describe the characteristics of blanked edges.MUCHA[4]and ACHOURI et al[5]separately acquired microstructures such as the sizeof grains on the blanked edges and the streamlinedistribution of metals.They found that thesignificant plastic deformation occurs and grainsare greatly refined in the blanked edges.ISMAIL et al[6]obtained the curve of yield stress on the blanked edges of non-oriented silicon steel with a thickness of0.65mm at the blanking speed of SPM80by using nano-indentation technology.The results indicated that significant work-hardening occurs in the zone around the blanked edges at a low blanking speed.GAUDILLIERE et al[7]performed high-speed blanking(14.6m/s)on C40steel using thesplit Hopkinson pressure bar test,and observed anadiabatic shear band in the blanked edges.SAPANATHAN et al[8]found that ultra-fine grains (diameter of grains lower than1μm)appeared in the microzone of the edges after attaining a crystal orientation map of the blanked edges of aluminum/ copper composite materials using the electron back-scatter diffraction(EBSD)technology.Using the finite element technology, RAFSANJANI et al[9]explored the temperature change of X30Cr13steel in the blanking process (blanking clearance of c=10%and punching speed of V=1000mm/s).They found that the localtemperature of the blanked edges is as high as387°C.By numerically simulating the high-speed blanking process(thickness of t=0.12mm,blankingclearance of c=6.5%t and punching speed of V=1000mm/s)of C5191phosphor bronze sheets, HU et al[10]demonstrated that the local temperature of the blanked edges reaches444°C. Local temperature rise has a significant effect on the fracture damage induced by blanking and microstructures of the blanked edges.Current research further systematicallyexplores various aspects of blanking such asmacroscopic blanked edge quality and numericalsimulation to deepen the understanding on high-speed blanking.However,it is difficult to profoundly and effectively analyze the blanking mechanism as little is known about the control and effects of microstructures that play critical roles on the localization of macroscopic deformation during blanking.In this study,the microstructural characteristics of the blanked edges and their evolution were investigated by conducting high-speed blanking tests.The results provide a basis for exploring the fracture mechanism of sheets during high-speed blanking.2Experimental2.1Preparation of blanking samplesTo describe the preparation process of theblanking samples for micro-measurements,theblanking sample is illustrated in Fig.1.Based on the micro-measurement of the blanked edges,the microstructure evolution of shear zone under different blanking conditions was analyzed(Zone I). The microscopic evolution of materials from the blanked edges to the matrix was analyzed based on the longitudinal section perpendicular to the direction of the blanked edges(Zone II).2.2Preparation of EBSD samplesEBSD technology is an effective method thatcan be used to determine crystal structure,orientation and related crystallographic information of samples.The diffraction Kikuchi band excited by electron beams emitted from the SEM on the surface of inclined samples was analyzed[11,12].Dao-chun HU,et al/Trans.Nonferrous Met.Soc.China 31(2021)692−702694The orientation analysis based on EBSD technology can acquire abundant information on the inner structure of crystals.It is common that only grain size,shape and distribution can be attained from microstructural and morphological images.Even though the image is processed using an image analysis system,only the quantitative information on morphology can be obtained.In contrast,in addition to diverse information on morphology,orientation imaging microscopy (OIM)can acquire various types of quantitative information such as grain orientation,phase distribution,grain (phase)boundary type,strain distribution and dislocation density [13,14].EBSD technology can demonstrate more information compared with direct observations.This information is crucial for comprehensively exploring the deformation law and microscopic mechanism of materials.Due to the requirement of the surface roughness requirement of samples in the EBSD test,the samples failed to be prepared in Zone I.To acquire the microstructures of deformed materials in Zone II on the blanked edges,blanking strips were cut and embedded in conductive inlay powder,as shown in Fig.2.The ends (marked in Fig.2(a))of the embedded samples all corresponded to the cutting planes (Fig.2(b))of the blanked edges.The surface stress layer was removed using twin-jet electropolishing after being mechanically polished.The scanning area of EBSD was 15μm from the blanked edges,as shown in Fig.2(b).The EBSD test was completed using a JSM−7001F/JEOL field emission scanning electron microscope equipped with EBSD.2.3Preparation of samples for TEM testTo test and analyze the microstructures of the blanked edges,and further discuss the evolution law of microstructures during blanking,two sample preparation methods were adopted.TEM samples perpendicular to the blanked edges (for observing microstructural changes from the blanked edges to the material matrix)and parallel to the edges (for observing the microstructures of the shear zone)were attained respectively,as shown in Fig.3.When preparing TEM samples perpendicular to the blanked edge,a disk with d 1.5mm was first obtained at the proper location of the blanked strip,as shown in Fig.3(a).The blanked edges of two semicircular samples were bonded (bonding the shear zone with the shear zone)and fixed using copper rings (Fig.3(b)).The blanked strip was subjected to one-way selective thinning by applying a Gatan PIPS−691ion milling,firstly from the shear zone along the fracture zone and then from the direction of the roll over zone.In this process,the position was broken down due to thinning in the shear zone (Fig.3(b)).Finally,the microzone forFig.1Schematic map of blankingsampleFig.2Preparation of samples for EBSD analysis:(a)Embedded blanked-sample;(b)Cutting plane of blanked edgesDao-chun HU,et al/Trans.Nonferrous Met.Soc.China31(2021)692−702695 Fig.3Preparation of TEM samples:(a,d)TEM sample preparation area;(b,e)Fixed by copper ring;(c,f)TEM observing area(III:TEM samples of longitudinal section;IV:TEM samples of blanked surface)the TEM test was situated within the red borderarea in Fig.3(c)to acquire the TEM morphologiesof four local microzones,near the shear zone,adjacent to the shear zone,adjacent to the matrix,and in the matrix.To ensure that the positions of the microzones(box zone)in different blanked stripsfor TEM test were consistent,the same parametersetting was adopted during one-way selectiveion-thinning.To reveal the evolution of the microstructuresin shear zones on the blanked edges at different punching speeds,TEM samples parallel to the blanked edges were prepared by referring to the preparation method[15]according to the following process:multiple samples were cut from the blanked strips that were3mm in length and about 0.3mm in width,as shown in the red border area of Fig.3(d)(the blanked edge cannot be damaged). Multiple samples were bonded with(G1)glue to ensure evenness of the blanked edges and fixed using copper rings(Fig.3(e)).The blanked strips were subjected to one-way selective thinning using the Gatan PIPS691ion beam thinner,only from the opposite of the blanked edges until the sample was broken down(Fig.3(e)).The microzones for the TEM test are displayed in Fig.3(f).The JEM−2100F/JEOL high-resolution TEM was usedto characterize the blanked edges.3Results and discussion3.1EBSD analysis of blanked edgesThe EBSD technology can be used to obtainthe microstructures of blanked edges and theirsurrounding zones to provide abundant informationabout the evolution of microstructures in theblanking process.Figure4(a)shows the image quality(IQ)of EBSD patterns in the deformed zoneof the blanked edge.According to the scanninginformation of the orientation mapping ofmicrozones,the quality of Kikuchi lines obtained inthe zone was demonstrated using different grayscales.However,the distortion and deformation of the crystals within the diffraction zone due to the effect of residual strain decrease the quality of EBSD patterns so that the IQ map is able to qualitatively reflect the distribution conditions of strains within the microstructures[16].Plastic deformation leads to the occurrence of a large number of dislocations in metal grains,whilst lattice distortion around the dislocation accumulates with the growth of dislocations.During the violentDao-chun HU,et al/Trans.Nonferrous Met.Soc.China31(2021)692−702 696Fig.4Orientation map of deformed zone on blanked edges(SPM600):(a)IQ map;(b)Local average misorientationdeformation,small-angle orientation changesappear in the local zones of materials to formvarious substructures including dislocation walls,microzones and even sub-grains.The orientationchange of local zones within metal grains under large deformation reflects the accumulation of thedislocations[17,18].The local averagemisorientation(Fig.4(b))attained based on theEBSD technology is sensitive to the subtle changeof orientation in grains,which can qualitativelymeasure the relative dislocation density of deformed metals[19].It can be seen that a large number of geometrically necessary boundaries (GNBs)and incidental dislocation boundaries (IDBs)are formed in the deformed zone of the blanked edges during the blanking.The grains in the zone are subjected to violent plastic deformation and stretched along the blanking direction to form strip-shaped microstructures,with a large misorientation of grains.In this case,a fragmentation layer of grains is formed.However, many high-angle GNBs for coordinating different strain zones have evolved into grain boundaries, and occupied a major proportion of the near shear zone.With the proceeding of blanking,grains are rotated so that the orientations of some grains are gradually consistent to form a special preferred orientation.The misorientation and size of grains in the blanked edges at a high punching speed are shown in Fig.5.It can be seen that the proportion of grains with high-angle orientation greatly increases in the blanked edge,and also fine grains with a small size are mainly found.This indicates that at an ultra-high punching speed,the local zone of the blanked edges presents a relatively low dislocation density(low local average misorientation),where micro-crystals(at the submicron order)are present.Furthermore,a large number ofhigh-angleFig.5Misorientation and size of grains in blanked edges at ultra-high punching speed:(a)Misorientation angle of blanked surface;(b)Grain size of blanked surfaceDao-chun HU,et al/Trans.Nonferrous Met.Soc.China31(2021)692−702697boundaries(large misorientation)are formed, accompanied with a certain preferred orientation (that is,special texture)of grains.Using Eulerian angles defined by Bunge,the random crystal orientation was realized by rotating from the initial orientation byφ1,Φandφ2,which were set in the range of0°−90°.The characteristic map of Euler orientation based onφ2at the interval of5°was selected to establish the orientation distribution function(ODF)for describing the textures of the diffraction microzones.According to the information shown in the pole figure(PF)and inverse pole figure(IPF),the textures of the blanked edges are shown in Fig.6.Through analysis using the INCA crystal software,strong{001}〈100〉cube textures (maximum pole densities of9and12)and secondarily strong{011}011〈〉textures(maximum pole densities of4and7)are formed on the blanked edges(SPM3000)at an ultra-high punching speed. According to the theory of orientation-induced nucleation,grains with the cubic orientation exhibit an advantage in the number of nucleation and grain size relative to grains with the other orientations.In contrast,cube textures are easily affected by various factors including nucleation and high-angle boundary migration,and are formed due to recrystallization annealing[20,21].Therefore,more {001}〈100〉cube textures are formed on the blanked edges at an ultra-high punching speed.3.2TEM characterization of blanked edgesAs described above,to determine the evolution of microstructures in the blanked edges and their surrounding deformed zone,Sample III perpendicular to the blanked edges was prepared by using the preparation method of planar samples and was observed.The TEM microstructures are shown in Fig.7.It can be seen that the blanked edge and its surrounding deformed zone show very different microstructural characteristics.Grains in the Zone A adjacent to the blanked edges were obviously stretched along the blanking direction under the combined effect of pressures and shear stress to form elongated grains with large deformation.The zone undergoes more significant deformation than the surrounding Zones B,C and D.After grains stretch to form the elongated thick-wall dislocation cells,dislocation of the cell walls increases and becomes entangled to form a dislocation wall. Furthermore,the dislocation wall collapses to form multiple sub-grains with a low misorientation underFig.6Textures of deformed zone in blanked edges:(a)ODF map;(b)PF map;(c)IPF mapDao-chun HU,et al/Trans.Nonferrous Met.Soc.China31(2021)692−702698Fig.7TEM images of blanked edges and corresponding affected zones:(a)Sample III(perpendicular to blanked surface);(b)Zone A;(c)Zone B;(d)Zone C;(e)Zone Dthe effect of heat.With the proceeding of blanking induced deformation,a small equiaxed zone is formed through rotation of sub-grains at the sub-boundary.In the subsequent deformation process,the dislocations climb and unlike dislocations on the sub-boundary,are mutually offset and disappear[22,23].There are many ultra-fine grains in the Zone A,with a grain size of 50−100nm.The diffraction patterns of the selected area also show distinct rings,which conform to EBSD characterization results that many high-angle boundaries in the Zone A.Some ultra-fine grains exhibit clear boundaries and low internal dislocation density.Thus,it can be inferred that the grains are typically formed by dynamic recrystallization[24].It was also found that the diffraction patterns of selected Zones D to A of the samples change from the discrete points to the discontinuous rings.These observations indicate that grains are constantly refined and the misorientation of grains constantly increases with the increase of strain.According to the rotational dynamical recrystallization(RDR)of sub-grains proposed by NESTCRCNKO and MEYERS[25],TEM was utilized to observe microstructures of the ultra-high-speed blanked edge.It was found that dislocation cells and tangles on the blanked edges constantly absorb dislocations under combined effects of large strain,plastic deformation at a high strain rate and temperature rise to transform into sub-grains and grains.On this condition,sub-boundaries are generated which form high-angle grain boundaries through short-distance movement.Dao-chun HU,et al/Trans.Nonferrous Met.Soc.China 31(2021)692−702699Moreover,sub-grains are stretched,broken and rotated under the effects of ultra-high strain,thus further from nano-crystals (Fig.8(b)).Fig.8Microstructures of adjacent area of blanked edges at ultra-high punching speed:(a)TEM morphology;(b)Nano-grains morphology;(c)Diffraction spots of nano-grainsFrom the diffraction patterns in the re-crystallized zone,it can be seen that the diffraction ring is more intact and smoother,and the number of layers of the ring is also more (Fig.8(c)).The results indicate that there is a large misorientation between grains consisting of high-angle boundaries,instead of sub-boundaries.Additionally,due to the thermal softening effect caused by local high temperature,the local zone is subjected to more violent plastic deformation.In this case,adiabatic shear is likely to occur to form adiabatic shear characterized by dynamic recrystallization [26,27].To further elucidate the evolution of microstructures in the shear zone on the blanked edges,Sample IV of the shear zone was prepared using the method for preparing cross-section samples.TEM observations of microstructures are displayed in Fig.9.It can be clearly seen that the grain size of the shear zone (Sample IV)is larger than that of the zone (Sample III)near the shear zone,perpendicular to the direction of the blanked edges.This implies that grains stretch along the blanking direction.It can also be found that a unique type of deformation twins occurred in the shear zone in the blanked edges.C5191phosphor bronze belongs to a face-centered cubic system,which has many slip systems and the deformation was mainly in the form of slip.However,the blanked edge was instantaneously subjected to a large shear stress during ultra-high-speed blanking.Under these conditions,the dislocation density significantly increased.Dislocations are entangled and piled to form a dislocation wall,thus delaying the initiation of the slip system.In this case,the occurrence of twins can compensate for the deficiency of the number of slip systems to satisfy the demand of great deformation [28,29].The twin boundaries in the figure are not straight but bend to some extent,which implies that lattice distortion is generated around the twin boundary.Moreover,a certain polygonization process occurs in and around the twins [30,31].With increasing blanking speed,more dislocation motions occur in the grains.The dislocation motion is hindered by the grain boundary to cause the piling up of a large number of dislocations in the vicinity of the grain boundary,thus forming new sub-grains.The newly generated sub-grains will then evolve into the structures with a high-angle grain boundary when the blanking speed is furtherincreased.Fig.9Microstructures of shear zoneDao-chun HU,et al/Trans.Nonferrous Met.Soc.China31(2021)692−702 700The dislocations are gradually entangled and converged to form the dislocation cell in theblanking process.As the blanking-induced deformation continues to grow,the dislocation cells grow in quantity whilst decreasing in size.Furthermore,the dislocation density of the cell wall further increases with the cell wall constantly moving to the grain boundary.Eventually,thedislocation tangles in the cell wall constantly converge resulting in the collapse of the dislocation cells,thus forming low-angle grain boundaries.Alarge number of sub-micro-scale unstable sub-grains are found in grains and small-angle textures rotate under the extrusion effects inducedby blanking of deformation.Furthermore,twins and sub-grains are broken,extruded and kinked,so numerous crystal defects are entangled andconverged to generate high distortion energy. Additionally,the sub-grains are gradually coarsened under the temperature-rise effect to form sub-grainswith apparent and high-angle boundaries.The sub-grains continue to grow as a crystal nucleus for recrystallization and finally grains are coarsened tohave significantly larger sizes than that of grains in the zone of Sample III.4Conclusions(1)Grains in the edges of C5191phosphorbronze sheets subjected to ultra-high-speedblanking undergo significant plastic deformation,which are stretched along the blanking direction toform strip-shaped microstructures.The misorientation of grains increases and thefragmentation layer of grains is formed.As theblanking process proceeds,grains are rotated,andso the orientations of some grains are graduallyconsistent to form a special{001}〈100〉cubetexture.(2)Diffraction patterns in the zones adjacent tothe blanked edges with different distances changefrom discrete points to discontinuous rings,showing different microstructural characteristics.There are many ultra-fine grains with the size of50−100nm in the Zone A adjacent to the blanked edges.In the zone,diffraction patterns appear as distinct rings,with clear grain boundaries and low internal dislocation density,indicating that they are typical grains formed by dynamic recrystallization.(3)Deformation twins are found in the shear zone of the blanked edges and are rotated and coarsened under the blanking-induced extrusion effect and local temperature-rise effect,which further form sub-grains with clear and high-angle boundaries.(4)During ultra-high-speed blanking,the local zone of the blanked edges is subjected to adiabatic shear due to high-speed deformation and adiabatic temperature rise,accompanied with dynamic recrystallization.This result suggests a new mechanism which largely differs from the common blanking mechanism. 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