Membranes, calendered microporous membranes, battery separators, and related methods

Abstract

Novel or improved microporous single or multilayer battery separator membranes, separators, batteries including such membranes or separators, methods of making such membranes, separators, and/or batteries, and/or methods of using such membranes, separators and/or batteries are provided. In accordance with at least certain embodiments, a multilayer dry process polyethylene/polypropylene/polyethylene microporous separator which is manufactured using the inventive process which includes machine direction stretching followed by transverse direction stretching and a subsequent calendering step as a means to reduce the thickness of the multilayer microporous membrane, to reduce the percent porosity of the multilayer microporous membrane in a controlled manner and/or to improve transverse direction tensile strength. In a very particular embodiment, the inventive process produces a thin multilayer microporous membrane that is easily coated with polymeric-ceramic coatings, has excellent mechanical strength properties due to its polypropylene layer or layers and a thermal shutdown function due to its polyethylene layer or layers. The ratio of the thickness of the polypropylene and polyethylene layers in the inventive multilayer microporous membrane can be tailored to balance mechanical strength and thermal shutdown properties.

Claims

1. A battery separator for a lithium battery comprising at least one microporous membrane having at least one outer surface or surface layer having a pore structure with a pore being an opening or a space between adjacent lamellae and which is bounded on one or both sides by a fibril or bridging structure between the adjacent lamellae and wherein at least a portion of the membrane contains groups of pores between adjacent lamellae with the lamellae oriented substantially along a transverse direction (TD) and the fibrils or bridging structures between the adjacent lamellae oriented substantially along a machine direction (MD) and an outer surface of at least some of the lamellae being substantially planar, and wherein the pore structure has at least one of: substantially trapezoidal or rectangular pores, pores with rounded corners, groups of pores with areas of missing or broken fibrils, groups of pores with a TD/MD length ratio of at least 4, groups of pores with a TD/MD length ratio of at least 6, groups of pores with a TD/MD length ratio of at least 8, groups of pores with a TD/MD length ratio of at least 9, groups of pores with at least 10 fibrils, groups of pores with at least 14 fibrils, groups of pores with at least 18 fibrils, groups of pores with at least 20 fibrils, pressed or compressed stacked lamellae, a uniform surface, a non-uniform surface, or combinations thereof.

2. The battery separator of claim 1 wherein the pore structure is closed as the result that a structure of lamellae is pressed or compressed in the thickness direction, and there are some extended micropores in a membrane surface direction.

3. The battery separator of claim 1 wherein the membrane is a polyolefin microporous membrane.

4. The battery separator of claim 3 wherein the membrane is a dry process membrane.

5. The battery separator of claim 1 wherein the membrane has a thickness from 5 μm to 25 μm and at least one of: pin removal force from 200-900 grams-force, air permeability from 50-250 Gurley seconds (JIS), porosity from 30%-90%, puncture strength from 50 g-600 g, MD/TD tensile strength ratio from 1.45-2.2, and Hot tip propagation value is from 2 to 4 mm.

6. The battery separator of claim 5 wherein the membrane has at least one of: a surface roughness from 0.0 to 1.5 um, a Tortuosity greater than 1, a Tortuosity greater than 2, a coefficient of friction of less than 0.3, a Pin Removal Force of from 200 to less than 800 grams-force, air permeability of from 50 to below 200 Gurley seconds (JIS), and a puncture strength of at least 400 g to 600 g.

7. The battery separator of claim 5 wherein the membrane is a single or multilayer dry process microporous polymer membrane wherein the membrane has been machine direction stretched and transverse direction stretched either sequentially or simultaneously, and has been subsequently calendered using at least pressure.

8. The battery separator of claim 7 wherein a roll used for calendering is smooth, textured, roughened, convex, concave, or otherwise patterned.

9. The battery separator of claim 1 wherein the membrane is a polymer membrane that comprises a polyolefin that includes a polypropylene, a polyethylene, a blend of polyolefins, a mixture of polyolefins, one or more co-polymers of a polyolefin, and combinations thereof.

10. The battery separator of claim 1 wherein the thickness of the membrane has been reduced by 2-80% by calendering.

11. The battery separator of claim 10 wherein the calendering is at least one of symmetrical and asymmetrical calendering.

12. The battery separator of claim 1 wherein the membrane is a polyethylene/polypropylene/polyethylene membrane and wherein the ratio of the thickness of the polyethylene/polypropylene/polyethylene layers ranges from 0.05/0.90/0.05 to 0.25/0.50/0.25.

13. The battery separator of claim 12 wherein the polyethylene/polypropylene/polyethylene microporous membrane has a percent porosity 20% to 75%.

14. The battery separator of claim 1 wherein the membrane has a thickness of less than 20 μm.

15. The battery separator of claim 1 wherein the membrane has a TD tensile strength of greater than 400 kgf/cm.sup.2.

16. The battery separator of claim 1 wherein the membrane is a ceramic coated microporous separator membrane comprising: a multilayer microporous membrane having a first and a second surface, a ceramic coating on at least one surface of said multilayer microporous membrane, wherein said ceramic coating comprises ceramic particles and a polymeric binder, and wherein at least one layer of said membrane is an MD stretched, TD stretched and calendered membrane.

17. The battery separator of claim 1 wherein the membrane is a single or multilayer dry process battery separator membrane, comprising at least one microporous polymer separator membrane wherein the at least one microporous polymer separator membrane has been machine direction stretched and transverse direction stretched either sequentially or simultaneously, and at least subsequently calendered using at least pressure to at least increase tortuosity.

18. A battery comprising the separator of claim 1.

19. A vehicle comprising the battery of claim 18.

20. A microporous membrane comprising at least one outer surface or surface layer having a pore structure with a pore being an opening or space between adjacent lamellae and which is bounded on one or both sides by a fibril or bridging structure between the adjacent lamellae and wherein at least a portion of the membrane contains pores between adjacent lamellae with the lamellae oriented substantially along a transverse direction (TD) and the fibrils or bridging structures between the adjacent lamellae oriented substantially along a machine direction (MD) and an outer surface of at least some of the lamellae being substantially flattened or planar, and wherein the pore structure has at least one of: substantially trapezoidal or rectangular pores, pores with rounded corners, lamellae across a width or the transverse direction, random pores, groups of pores with areas of missing or broken fibrils, groups of pores with a TD/MD length ratio of at least 4, groups of pores with a TD/MD length ratio of at least 6, groups of pores with a TD/MD length ratio of at least 8, groups of pores with a TD/MD length ratio of at least 9, groups of pores with at least 10 fibrils, groups of pores with at least 14 fibrils, groups of pores with at least 18 fibrils, groups of pores with at least 20 fibrils, pressed or compressed stacked lamellae, a uniform surface, a non-uniform surface, or combinations thereof.

21. The microporous membrane of claim 20 wherein the pore structure is closed as the result that a structure of lamellae is pressed or compressed in the thickness direction, and there are some extended micropores in a membrane surface direction.

22. The microporous membrane of claim 20 wherein the membrane comprises a polyolefin.

23. The microporous membrane of claim 22 wherein the membrane is a dry process membrane.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a schematic diagram of a manufacturing process for a MD uniaxial stretched trilayer polypropylene/polyethylene/polypropylene (PP/PE/PP) microporous membrane.

(2) FIG. 2 is a schematic diagram of an inventive process described herein for manufacturing an MD/TD biaxial stretched and calendered (MD/TD/C) trilayer polypropylene/polyethylene/polypropylene (PP/PE/PP) microporous membrane.

(3) FIG. 3 is a schematic diagram of an inventive process described herein for manufacturing a MD/TD stretched and calendered trilayer polyethylene/polypropylene/polyethylene (PE/PP/PE) microporous membrane.

(4) FIG. 4 is a Scanning Electron Micrograph (SEM) image of the surface of a Comparative Example 1 (CE 1) at a magnification 20,000×.

(5) FIG. 5 is a Scanning Electron Micrograph (SEM) image of the surface of a Comparative Example 2 (CE 2) at a magnification 20,000×.

(6) FIG. 6 is a Scanning Electron Micrograph (SEM) image of a cross sectional view of CE 2 at a magnification 3,000×.

(7) FIG. 7 is a Scanning Electron Micrograph (SEM) image of the surface of a Comparative Example 3 (CE 3) at a magnification 5,000×.

(8) FIG. 8 is a Scanning Electron Micrograph (SEM) image of the surface of CE 3 at a magnification 20,000×.

(9) FIG. 9 is a Scanning Electron Micrograph (SEM) image of a cross sectional view of CE 3 at a magnification 5,000×.

(10) FIG. 10 is a Scanning Electron Micrograph (SEM) image of the surface of exemplary inventive Example 1 at a magnification 20,000×.

(11) FIG. 11 is a graph that includes Thickness values of PP/PE/PP trilayer including Comparative Example 1, Comparative Example 2 and Comparative Example 3 and PE/PP/PE trilayer including Comparative Example 4, Comparative Example 5 and Example 1.

(12) FIG. 12 is a graph that includes TD tensile strength values of PP/PE/PP trilayer including Comparative Example 1, Comparative Example 2 and Comparative Example 3 and PE/PP/PE trilayer including Comparative Example 4, Comparative Example 5 and Example 1.

(13) FIG. 13 is a bar chart that includes a comparison of TD tensile strength of dry process microporous membranes Comparative Examples 4, Comparative Examples 5 and Example 1.

(14) FIG. 14 is a graph that includes MD tensile strength values of PP/PE/PP trilayer including Comparative Example 1, Comparative Example 2 and Comparative Example 3 and PE/PP/PE trilayer including Comparative Example 4, Comparative Example 5 and Example 1.

(15) FIG. 15 is a Scanning Electron Micrograph (SEM) image of the surface of Comparative Example 4 PE/PP/PE after MD stretching at a magnification of 5,000×.

(16) FIG. 16 is a Scanning Electron Micrgraph (SEM) image of a cross sectional view of Comparative Example 4 at a magnification of 1,500×.

(17) FIG. 17 is a Scanning Electron Micrograph (SEM) image of the surface of Comparative Example 5 PE/PP/PE after MD stretching and TD stretching at a magnification of 5,000×.

(18) FIG. 18 is a Scanning Electron Micrograph (SEM) image of a cross sectional view of Comparative Example 5 at a magnification of 3,000×.

(19) FIG. 19 is a Scanning Electron Micrograph (SEM) image of the surface of Example 1 PE/PP/PE after MD stretching, TD stretching, and calendering at a magnification of 5,000×.

(20) FIG. 20 is a Scanning Electron Micrograph (SEM) image of a cross sectional view of Example 1 at a magnification of 5,000×.

(21) FIG. 21 is before and after Scanning Electron Micrograph (SEM) images of cross sectional views showing symmetrical calendering of Comparative Example 5 after TD stretching on the left (A) and the same membrane after calendering on the right (B) at a magnification of 3,000× and 3,500× respectively. Both the top and bottom polyethylene layers were reduced to 1.8 μm. Note that Comparative Example 4 (MD only) can be a precursor for Comparative Example 5 (MD and TD) and that Comparative Example 5 (MD/TD) can be a precursor for Example 1 (MD/TD/C).

(22) FIG. 22 is side by side Scanning Electron Micrograph (SEM) images of cross sectional views showing asymmetrical calendering of Comparative Example 5 after calendering on a magnification of 6,000×. The top polyethylene layer was reduced to 1.72 μm and the bottom layer to 2.19 μm.

(23) FIG. 23 shows respective surface roughness diagrams of respective stretched trilayer films at −10% TD and 200% TD stretch respectively.

(24) FIG. 24 shows 3-D quantification diagrams of surface roughness of TD stretched trilayer film (A) vs TD stretched trilayer film (B).

(25) FIG. 25 is a graph depicting the pin removal performance after the incorporation of lithium stearate.

(26) FIG. 26 is a graph depicting the pin removal performance with 0%, 5%, and 2% lithium stearate incorporated as compared to comparative competitor trilayer membranes.

(27) FIG. 27 is a set of nine Scanning Electron Micrograph (SEM) images of the surface of three different TD stretched products. Panel 1 (top row from left to right three SEMs) shows the TD stretched EZ2090 product membrane at 5,000×, 20,000× and 20,000× magnification. Panel 2 (center row from left to right three SEMs) shows the TD stretched EZ2090 product membrane that has been further TD stretched at 5,000×, 20,000× and 20,000× magnification. Panel 3 (bottom row from left to right three SEMs) shows the TD stretched EZ2090 product membrane that has been further TD stretched and calendered at 5,000×, 20,000× and 20,000× magnification.

(28) FIG. 28 is a set of three Scanning Electron Micrograph (SEM) images (A), (B), and (C) of the cross section of two TD stretched precursors (A) and (B) at 3,000× magnification and a calendered product (C) at 3,500× magnification and a very schematic representation of thickness and of tortuosity (pore path) shown in at least one PE layer of each membrane.

(29) FIG. 29 is a schematic surface diagram showing the spreading apart of lamellae to form micropores bounded by bridging structures or fibrils in a typical MD stretch dry process. The pores are more slit like and oriented in the MD direction (see FIG. 4).

(30) FIG. 30 is a combination of FIGS. 19 and 21 (B) together with a schematic figure of a trilayer membrane or product showing that the Side A surface SEM of FIG. 19 is of the upper surface layer of FIG. 21 (B) and that at least the upper surface of the product has a unique pore structure.

(31) FIG. 31 is modified version of surface SEM of FIG. 19 modified to highlight the pores, pore structure, surface structure, and particular selected portions or pore areas designated 1-5.

(32) FIGS. 32, 33 and 34 are respective enlarged views of portions of the modified surface SEM of FIG. 31.

(33) FIGS. 35, 36 and 37 are respective enlarged views of portions of the surface SEM of FIG. 19.

DETAILED DESCRIPTION OF THE INVENTION

(34) In accordance with at least certain embodiments, the present invention is directed to a multilayer polyolefin membrane for a rechargeable lithium battery which is manufactured using a lamination process, a coextruded process or a combination of the two processes. In at least certain embodiments, the multilayer polyolefin membrane may include polypropylene and polyethylene, or a blend, mixture or copolymer of polypropylenes and polyethylenes. Two non-limiting examples of a multilayer polyolefin membrane may be a polypropylene/polyethylene/polypropylene (PP/PE/PP) microporous membrane and a polyethylene/polypropylene/polyethylene (PE/PP/PE) microporous membrane. Furthermore embodiments may be possible by changing the number of PP and PE layers in the multilayer membrane and alternating the order of stacking of PP and PE layers in the multilayer membrane.

(35) FIG. 2 is a schematic of a manufacturing process for the polypropylene/polyethylene/polypropylene (PP/PE/PP) microporous membrane embodiment of the membrane described herein, where two layers of PP and one layer of PE are stacked with the PE layer as an inner layer and the two PP layers as outer layers forming a nonporous PP/PE/PP trilayer membrane. The stacked nonporous PP/PE/PP trilayer membrane is laminated to bond the layers together. The laminated nonporous trilayer is then annealed followed by a machine direction (MD) stretching step to make the membrane microporous. The inventive microporous PP/PE/PP trilayer membrane described herein is produced by transverse direction (TD) stretching of the MD stretched microporous PP/PE/PP trilayer membrane, followed by a subsequent calendering step of the ‘MD-TD stretched’ microporous PP/PE/PP trilayer membrane to reduce the membrane's thickness, reduce roughness, reduce percent porosity, increase TD tensile strength, increase uniformity, and/or reduce TD splittiness. A possibly preferred membrane or product may be manufactured using an exemplary inventive process described herein which includes stretching and a subsequent calendering step such as a machine direction stretching followed by transverse direction stretching (with or without machine direction relax) and a subsequent calendering step as a possibly preferred means to reduce the thickness of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, to reduce the percent porosity of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, and/or to improve the strength, properties, and/or performance of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, such as the puncture strength, machine direction and/or transverse direction tensile strength, uniformity, wettability, coatability, runnability, compression, spring back, tortuosity, permeability, thickness, pin removal force, mechanical strength, surface roughness, hot tip hole propagation, and/or combinations thereof, of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, and/or to produce a unique structure, pore structure, material, membrane, base film, and/or separator. The inventive process may produce 10 μm or less single or multilayer microporous membranes. In addition, the calendering process may use uniform or non-uniform heat, pressure and/or speed to selectively densify a heat sensitive material, to provide a uniform or non-uniform calender condition (such as by use of a smooth roll, rough roll, patterned roll, micro pattern roll, nano pattern roll, speed change, temperature change, pressure change, humidity change, double roll step, multiple roll step, or combinations thereof), to produce improved, desired or unique structures, characteristics, and/or performance, to produce or control the resultant structures, characteristics, and/or performance, and/or the like.

(36) FIG. 3 is a schematic of a manufacturing process for the possibly preferred polyethylene/polypropylene/polyethylene (PE/PP/PE) microporous membrane embodiment of the inventive membrane described herein, where two layers of PE and one layer of PP are stacked with the PP layer as an inner layer and the two PE layers as outer layers forming a nonporous PE/PP/PE trilayer membrane. The stacked nonporous PE/PP/PE trilayer membrane is laminated to bond the layers together. The laminated nonporous trilayer is then annealed followed by a machine direction (MD) stretching step to make the membrane microporous. The inventive microporous PE/PP/PE trilayer membrane described herein is produced by transverse direction (TD) stretching of the MD stretched microporous PE/PP/PE trilayer membrane, followed by a subsequent calendering step of the ‘MD-TD stretched’ microporous PE/PP/PE trilayer membrane to reduce the membrane's thickness, reduce roughness, reduce percent porosity, increase TD tensile strength, increase uniformity, and/or reduce TD splittiness. A possibly preferred PE/PP/PE trilayer membrane or product may be manufactured using an exemplary inventive process described herein which includes stretching and a subsequent calendering step such as a machine direction stretching followed by transverse direction stretching (with or without machine direction relax) and a subsequent calendering step as a possibly preferred means to reduce the thickness of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, to reduce the percent porosity of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, and/or to improve the strength, properties, and/or performance of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, such as the puncture strength, machine direction and/or transverse direction tensile strength, uniformity, wettability, coatability, runnability, compression, spring back, tortuosity, permeability, thickness, pin removal force, mechanical strength, surface roughness, hot tip hole propagation, and/or combinations thereof, of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, and/or to produce a unique structure, pore structure, material, membrane, base film, and/or separator. The inventive process may produce 10 μm or less multilayer microporous membranes. In addition, the calendering process may use uniform or non-uniform heat, pressure and/or speed to selectively densify a heat sensitive material, to provide a uniform or non-uniform calender condition (such as by use of a smooth roll, rough roll, patterned roll, micro pattern roll, nano pattern roll, speed change, temperature change, pressure change, humidity change, double roll step, multiple roll step, or combinations thereof), to produce improved, desired or unique structures, characteristics, and/or performance, to produce or control the resultant structures, characteristics, and/or performance, and/or the like.

(37) Table 1 lists membrane thickness information together with performance data on ‘MD stretched’, ‘MD-TD stretched’ and ‘MD-TD-calendered’ dry process comparative examples PP/PE/PP microporous trilayer membranes and membrane thickness information together with performance data on the ‘MD-stretched’, ‘MD-TD stretched’ and inventive ‘MD-TD-calendered’ PE/PP/PE inverse trilayer microporous membranes. Comparative Example 1 is a 38 μm PP/PE/PP microporous trilayer membrane which has been uniaxial MD stretched only. The ratio of the thickness of the PP and PE layers in Comparative Example 1 trilayer configuration is 0.33/0.33/0.33 (PP/PE/PP) indicating that the PP and PE layers are equivalent in thickness. The MD tensile strength and TD tensile strength of Comparative Example 1 are 1630 kgf/cm.sup.2 and 165 kgf/cm.sup.2, respectively, indicating that MD direction tensile strength is stronger than TD direction tensile strength when a membrane is stretched uniaxially in one direction (MD direction). FIG. 4 is a Scanning Electron micrograph of the surface of Comparative Example 1 showing the microporous structure may be composed of row nucleated crystalline lamellae with fibrillar tie chain-like structures interconnecting the crystalline lamellae. The pores have a rectangular slit-shape which is characteristic of dry process MD stretched microporous membranes.

(38) TD stretching (in a direction perpendicular to MD) of Comparative Example 1 produces Comparative Example 2. FIG. 5 shows a SEM micrograph of Comparative Example 2 where the microstructure indicates transverse stretching appears to have a marked effect on the appearance of the row nucleated crystalline lamellae where the crystalline lamellae appear more elongated in a transverse direction. As a result, TD tensile strength of Comparative Example 2 is higher and may be nearly 40% higher than the TD tensile strength of Comparative example 1. This increase in TD tensile strength may be due to TD stretching on the crystalline lamellae and interconnecting fibrillar structures. FIG. 6 is a cross sectional view of Comparative Example 2 showing the more open porous structure of the inner PE microporous layer sandwiched by outer PP microporous layers. The shape of the Comparative Example 2 MD/TD stretched pores may appear round-shaped.

(39) FIG. 7 shows the SEM micrograph of the surface of Comparative Example 2 at a magnification of 5,000×.

(40) The process described herein in FIG. 2 includes a ‘combined TD stretching and subsequent calendering’ of a MD stretched Comparative Example 3 (MD/TD/C) microporous membrane may be produced by calendering Comparative Example 2. The calendering process involves heat and pressure and may reduce the thickness of the membrane in a controlled fashion. The surface of Comparative Example 3 is shown at 20,000× magnification in FIG. 8. A cross sectional view of Comparative Example 3 is show in FIG. 9 where the inner PE layer may appear to be condensed and densified as compared to FIG. 6. The membrane thickness of Comparative Example 3 is reduced from 27.4 μm to 10.3 μm after combined TD stretching and subsequent calendering. A thin microporous membrane is desirable as a separator membrane for a rechargeable lithium ion battery because a thinner separator membrane allows more anode/separator/cathode material to be placed in a battery resulting in a higher energy and higher power density battery.

(41) While the multilayer PP/PE/PP separator membrane has enjoyed great commercial success as a separator membrane in a lithium ion high energy, high power density rechargeable battery, battery manufacturers for mobile and electric vehicle applications are showing keen interest in coating the microporous separator membrane with a polymeric-ceramic containing coating in order to improve the thermal safety of a battery. Due to the relatively low surface tension of polypropylene (30 to 32 dyne-cm) as compared to polyethylene (34 to 36 dyne-cm), polyethylene may be easier to coat than PP when the coating is a polymeric-ceramic coating. In addition, PE is known to have lower pin removal than PP in the battery cell winding process. The present MD/TD/C process of the PP/PE/PP membrane (or of a PP, PP/PP, or PP/PP/PP membrane) can enhance coating adhesion and reduce pin removal of the outer PP layers or outer PP surfaces.

(42) In accordance with at least selected embodiments, the present application is directed to a novel or improved microporous multilayer dry process battery separator membrane, separators, batteries including such separators, methods of making such membranes, separators, and/or batteries, and/or methods of using such membranes, separators and/or batteries where polyethylene, a blend of different polyethylenes or a mixture of polyethylene and polypropylene are used as outer layers of a multilayer microporous membrane and polypropylene may be used as an inner layer(s). In accordance with at least certain embodiments, the present invention is directed to a multilayer polyolefin microporous membrane where polyethylene, a blend of different polyethylenes or a mixture of polyethylene and polypropylene are used in one or more outer layers of a multilayer microporous membrane and polypropylene may be used as one or more inner layers where the lay-up configuration maybe, but is not limited to, PE/PP/PE.

(43) In accordance with at least selected embodiments, the present application is directed to, but is not limited to, a PE/PP/PE dry microporous membrane which is manufactured using a combination of machine direction, transverse direction and calendering steps as shown in FIG. 3. The order of these three steps is important in the overall separator and battery performance properties of the PE/PP/PE microporous membrane. MD stretching may provide rectangular slit-shaped micropores, whereas the TD stretching may alter the amount of crystallinity and the amorphous content of membrane resulting in an improvement in TD tensile strength, reduced splittiness and higher percent porosity. The resulting pore shape of an outer PP layer after biaxial stretching is substantially round pores (FIG. 5), whereas FIG. 17 demonstrates resulting pore shape after biaxial stretching of a PE outer layer (pores that have an ellipsoid appearance). The ellipsoid pore is characterized by a flattened top and rounded edges. FIG. 19 shows what the pores of FIG. 17 look like after calendering (MD/TD/C). The compressed ellipticity of the biaxially stretched and calendered porous membrane (FIG. 19) may contribute to increased compression resistance or reduced spring back capacity. Combining MD and TD with a subsequent calendering step may produce an overall thinner PE/PP/PE microporous membrane. FIG. 21 shows a 21 μm biaxially stretched inverted trilayer porous membrane reduced to an 11.5 μm porous membranes post-calendering, a 50% reduction in thickness. The outer polyethylene layers were reduced by approximately 64% from approximately 5 μm each to approximately 1.8 μm each. The inner polypropylene layer was reduced from approximately 11 μm to approximately 7.7 μm. FIG. 21 demonstrates symmetrical reduction of layer thickness, while FIG. 22 demonstrates that the reduction in thickness may be selectively asymmetrical. In this example the top polyethylene layer was reduced to 1.72 μm and the bottom layer was reduced to 2.19 μm. The asymmetric or controlled calendering may provide optimal or controlled protection of dendrite growth (anode side) and oxidation resistance (cathode side). TD stretching may involve an increase in percent porosity in the microporous membrane. A calendering step following TD stretching may provide as means to modify the increase in percent porosity which may occur during TD stretching, and lower the overall percent porosity of the MD/TD/Calendered microporous membrane. Table 1 demonstrates the increase in porosity that comes after TD stretching and the reduction in porosity after calendering. In the monoloayer polypropylene examples after calendering the porosity is returned to it is MD stretching value, from 66% back to 40%.

(44) TABLE-US-00001 TABLE 1 PP Monolayer P/E/P EZ1290 EZ2590 2340 2340(B313) Property MD TD TDC MD TD TDC MD TD TDC MD TD TDC Thickness 26 11 12 56 25 15 39.2 19.8 15 37.6 25.8 13.5 Porosity 40 76 40 66 41 42.7 59.5 52 43.9 60.4 52.79 Gurley 370 35 129 900 60 246 711.8 47.1 89 1015 40 148 Puncture 488.5 190.2 800 425 440 704.4 226 314 677.5 296 295 MD Tensile 1700 677 1900 870 1351 1720.1 682 849 1808.8 621 1127 TD Tensile 150 535 150 550 687 132.3 440.3 431 140.6 313 528 E/P/E X137 X129 Property MD TD TDC MD TD TDC Thickness 55.3 33.4 24 35.6 25.5 13.2 Porosity 38.38 67.3 54.02 43.7 68.81 53 Gurley 1550 70.2 105 563.9 34 51 Puncture 629.2 261.7 316 427.5 198.1 201 MD Tensile 1955.3 650 1186 1801.7 539.5 927 TD Tensile 157 353.4 388 147.4 315.5 473

(45) The inventive MD/TD/Calendering process for manufacturing a PE/PP/PE microporous membrane may provide an inventive approach to 1) overcoming the thinness limitation of MD stretching-only process and produce thicknesses less than 10 μm, 2) controlling the increase in porosity which may occur in the TD stretching process, 3) produce a mechanically stronger microporous membrane with improved TD tensile strength, 4) produce a separator membrane with higher surface tension to facilitate ease of coating and excellent coating adhesion and 5) produce a separator with lower pin removal than a separator having outer PP layers which may produce higher battery cell yields in the winding step in the manufacture of a lithium ion battery using PE/PP/PE trilayer configuration.

(46) When stretchinq membranes in the MD and TD directions and subsequently calendering as described herein, the membranes may have several improved characteristics including improved mechanical strength in a thinner separator. Some of the resulting membranes however may have reduced permeability. To prevent lowering the permeability below a desired level, the surface roughness may be controlled. Analysis of membranes with trilayer constructions show a significant amount of surface roughness prior to TD stretching. The multilayer construction overall provides improved mechanical strength as compared to a monolayer construction. When coupled with its innate surface roughness characteristics, an improved stretched and/or calendered multilayer membrane may also have improved pin removal performance (reduced COF). Analysis also shows that when multilayer membranes are stretched in the TD direction and then calendered the surface of the membrane may become even less rough (or have a more uniform surface roughness or a controlled surface roughness (which can also reduce or control pin removal forces, enhance or control thickness uniformity, etc.). FIGS. 23 shows a 3-dimensional laser scanning microscope image of a trilayer 2.1x MD only stretched film (−10% TD) and shows a 4.5x TD stretched trilayer film (200%). The surface roughness is significantly reduced in the TD stretched film. Those films with increased or controlled roughness on either a milli or micro scale may have improved pin removal performance. FIG. 24 shows a quantification of the membranes' roughness pre (A) and post TD stretching (B). Table 2 shows surface roughness (low vs high thickness) and the resultant COF.

(47) TABLE-US-00002 TABLE 2 Sample Sa(μm) Sz(μm) COF A 0.258 3.14 0.368 B 0.234 2.77 0.357 X129TD 1.169 13.22 0.231 X129TDC 0.586 7.14 0.281 C 0.272 3.01 0.361

(48) After TD stretching and/or calendering there may be a decrease in surface roughness. To prevent reduced permeability post TD stretching, an inventive non-uniform, patterned or roughened calendering roll (or controlled non-uniform calendering) may be used to intentionally rebuild or control the surface roughness, to control tortuosity, to control the reduction in permeability, to control pin removal or COF, to control uniformity, to control coatability, to control mechanical strength, to control compressibility and/or bounce back, to control hot tip hole propagation, to control thickness, or combinations thereof. The use of such inventive calender rolls may improve pin removal and increase the membranes tortuosity. When examining and evaluating the high temperature melt integrity (HTMI) properties of a TD stretched and “roughened” calender membranes, the hot tip hole propagation test may be deployed. This test may show that those membranes that have been TD stretched and calendered with roughened calender rolls that the resulting hole after hot hip contact is significantly smaller. As previously stated, a roughened surface may help to improve pin removal performance. Table 2 lists the COF and roughness measurements. COF and roughness is correlated. Pin removal performance may also be improved in TD stretched and calendered membranes by incorporating additives into the membrane, along the surface of, and/or in the resin mix. Metallic stearates may be further incorporated into TD stretched and calendered films to improve pin removal performance (and a reduction in COF). FIG. 25 demonstrates the effect of incorporating lithium stearate (LiSt) into membranes. When adding 5% LiSt into membranes, the pin removal force was reduced at 50 g, 200 g, and 350 g when compared to control samples with no LiSt. The incorporation of LiSt in monolayer membranes shows improved pin removal performance even when compared with comparative competitive trilayer membranes. In TD strectched and calendered samples with LiSt incorporated there may be improvements not only in pin removal performance but also lower Gurley performance. The incorporation of Li St may also increase melting point temperature from approximately 155° C. to approximately 220° C. and broaden the melt flow index (MFI) range from approximately 1.2-1.7 to 0.4-5.0, making the resulting membrane suitable for higher temperatures. In certain instances the incorporation of LiSt may also allow for the membranes to be extruded at lower temperatures of approximately 10-30° C. depending on the resin MFI, acting as a plasticizer. Calendering with a roughened, patterned or non-uniform roll may also improve pin removal, wettability, adhesion, and/or the like.

(49) In accordance with selected embodiments, one may add one or more metallic stearates (such as lithium, sodium, calcium, magnesium, zinc, and combinations thereof, such as lithium and calcium stearates). Lithium stearate and/or calcium stearate is preferred. LiSt can serve as a surfactant or wetting agent and to reduce pin removal and/or the COF, especially for the surface of a PP layer or membrane. In accordance with selected embodiments, there may be provided a method for removing a pin from a battery assembly by the step of providing a separator comprising: a microporous membrane having an exterior surface portion of polypropylene, the polypropylene including at least 500 ppm of metallic stearate, preferably lithium stearate and/or calcium stearate.

(50) A PE/PP/PE ‘machine direction/transverse direction/calendered’ trilayer microporous membrane that has a thickness less than 10 μm, may have several advantages that may improve battery design and performance. A 10 μm or less multilayer polyolefin microporous separator membrane may take up less space inside a battery and may allow for more electrode active material to be packed in a battery cell for higher energy density and higher rate capability. Furthermore the combination of a machine direction and subsequent transverse stretching step followed by a calendering step may provide a promising method to achieve a microporous membrane that has excellent machine direction tensile strength and transverse direction tensile strength together with controlled percent porosity and a thermal shutdown function while having a thickness less than 10 μm. The unexpected level of improvement in tensile properties of the inventive PE/P/PE inventive separator microporous membrane described herein produced using MD stretching, TD stretching and calendering may achieve the machine direction tensile strength and transverse direction tensile strength levels similar to that of wet process PP and/or PE-containing multilayer microporous membrane without the environmental issues associated with a wet process manufacturing process.

(51) Table 3 lists performance data on the comparative membranes and inventive membranes described herein. Comparative Example 4 is a 32.4 μm PE/PP/PE microporous trilayer membrane which has been MD stretched. The ratio of the thickness of the PP and PE layers in the PE/PP/PE trilayer configuration is 0.19/0.63/0.19 indicating that the outer PE layers are thinner than the inner PP layer.

(52) TABLE-US-00003 TABLE 3 CE 1 CE 2 CE 3 Trilayer configuration PP/PE/PP PP/PE/PP PP/PE/PP PP/PE/PP ratio .33/.33/.33 .33/.33/.33 .33/.33/.33 Thickness, μm 38   27.4 10.3 Gurley JIS, s 780 370 176 MD tensile, kgf/cm.sup.2 1630 610 1560 TD tensile, kgf/cm.sup.2 165 286 665 MD % Elongation 48 54 TD % Elongation 954 103 51 Puncture Strength, 686 295 179 Electrical Resistance, 4.3 na 0.9 ohm-cm.sup.2 CE 4 CE 5 Ex. 1 Ex. 2 Ex. 3 Trilayer configuration PE/PP/PE PE/PP/PE PE/PP/PE PE/PP/PE PE/PP/PE PE/PP/PE ratio .19/.63/.19 .19/.63/.19 .19/.63/.19 .19/.63/.19 .19/.63/.19 Thickness, μm 32.4 20.9 7.5 9.4 8.8 Gurley JIS, s 494 24.8 159 176 126 MD tensile, kgf/cm.sup.2 2078 573 1581 1173 1262 TD tensile, kgf/cm.sup.2 123 256 543 488 468 MD % Elongation 115 32 345 106 123 TD % Elongation 5.14 2.6 75 8.2 77 Puncture Strength, TBD TBD 160 165 167 % Porosity 46 68 40 33 TBD Electrical Resistance, 1.84 0.51 1.27 0.97 0.6 ohm- cm.sup.2 Calendering na na 60 60 60 Temperature, ° C. Calendering Pressure, psi na na 200 125 50 Calendering Speed, na na 80 80 80 ft/min.
The MD tensile strength and TD tensile strength of Comparative Example 4 are 2078 kgf/cm.sup.2 and 123 kgf/cm.sup.2, respectively, indicating that MD direction tensile strength is stronger than TD direction tensile strength when a membrane is stretched uniaxially in one direction (MD direction).

(53) TD stretching (in a direction perpendicular to MD) of Comparative Example 4 produces Comparative Example 5. As a result of TD stretching, TD tensile strength of Comparative Example 5 is more than double the TD tensile strength of Comparative Example 4. This increase in TD tensile strength may be due to TD stretching on the crystalline lamellae and interconnecting fibrillar structures.

(54) In at least certain embodiments, the TD tensile strength of the inventive membrane may be further improved by the addition of a Calendering step following TD stretching. The calendering process which involves heat and pressure may reduce the thickness of a porous membrane. FIG. 10 is an SEM micrograph of the surface of inventive Example 1 membrane where the surface of the PE/PP/PE porous membrane appears slightly modified due to the lower melting temperature of PE during the application of heat and pressure of the calendering step. However, the calendering process step may have recovered the loss in the MD and TD tensile strength caused by TD stretching. Furthermore, the increase observed in MD and TD tensile strength with calendering may create a more balanced ratio of MD and TD tensile strength which may be beneficial to the overall mechanical performance of the inventive membrane. Examples 2 and 3 may also be produced by varying the heat and pressure if the calendering conditions. Example 2 and 3 were produced using the same calendering temperature of 60 deg C. and a line speed of 60 ft/min as used in Example 1, while the calendering pressure was varied from 50 to 200 psi. The higher pressure may provide a thinner separator.

(55) At least one inventive process described herein comprises a ‘combined TD stretching and subsequent calendering’ of a MD stretched microporous membrane. Using the inventive process described herein of a combined TD stretching and subsequent calendering, the membrane thicknesses of Example 1, Example 2 and Example 3 are 7.5 μm, 9.4 μm and 8.8 μm, respectively. A microporous membrane with a thickness less than 10 μm is desirable as a separator membrane for a rechargeable lithium ion battery because a thinner separator membrane allows more anode and cathode active material to be placed in a battery resulting in a higher energy and higher power density battery.

(56) In at least certain selected embodiments the improved separator may be a monalayer porous membrane that has been biaxially stretched and calendered. Table 4 list properties of biaxially stretched monolayer polypropylene (MD/TD) compared to biaxially stretched and calendered monolayer polypropylene (MD/TD/C). The calendered membrane is thinner by up to 50% while maintaining good ER performance and strength capabilities. FIG. 27 Panel 1 (top 3 SEMS) shows a biaxially stretched membrane (MD stretched, followed by TD stretched with MD relax) that has substantially round or sphereical pores in a very uniform pattern in at least the outer PP layer thereof. FIG. 27 Panel 2 (middle 3 SEMS) shows a biaxially stretched membrane (MD stretched, followed by TD stretched with MD relax, followed by additional TD stretching) that has substantially oval or elongated in the TD shaped pores in at least the outer PP layer thereof. FIG. 27 Panel 3 (bottom 3 SEMS) shows a biaxially stretched and calendered membrane (MD stretched, followed by TD stretched with MD relax, followed by additional TD stretching, and then calendered [pressure or compression in the Z direction]) that has pores that are oval or ellipsoid in shape with condensed lamellae across the width in at least the outer or surface PP layer.

(57) TABLE-US-00004 TABLE 4 MDTDC MDTDC Properties EZ2090 EZ2090 EZ2590 EZ2590 Thickness 20 10.64/0.37 25 16.4/0.50 (um)/stdev Porosity, % 65% 41% 69% 53% Gurley (JIS), 65 144 66 150 seconds MD/TD Shrinkage 8.0/0.2  9.0/1.5 4.0/0.5 6.4/0.9 @ 105 C. MD/TD Shrinkage  12/0.5 12.1/2.3 8.5/0.5 8.9/2.2 @ 120 C. Puncture Strength, 380 358 425 480 grams MD Tensile (kg/cm2) 950 1700 870 1252 TD Tensile (kg/cm2) 650 1146 550 655 ER (ohm-cm2) 0.7 0.93 0.8 1.0

(58) FIG. 11 is a plot of the thickness of PP/PE/PP and PE/PP/PE trilayer microporous membranes using MD stretch only, MD stretching followed by TD stretching, and the inventive process described herein of MD stretching followed by TD stretching and subsequent Calendering to prepare a PE/PP/PE microporous membrane. The thickness of the membrane is observed to decrease when the MD stretched membrane is TD stretched. Furthermore, calendering further reduces the thickness of the MD-TD stretched membrane. Calendering may provide a reliable method to reduce the thickness of a microporous membrane in a controlled fashion.

(59) FIG. 12 is a plot of the TD tensile strength of PP/PE/PP and PE/PP/PE trilayer microporous membranes using MD stretch only, MD stretching followed by TD stretching, and the inventive process described herein of MD stretching followed by TD stretching and subsequent Calendering to produce a MD/TD/Calendered PE/PP/PE microporous membrane. The TD tensile strength of the PP/PE/PP and PE/PP/PE trilayer microporous membranes may increase of approximately 4 to 5 fold when the membrane are produced using inventive process described herein which combines MD stretching followed by TD stretching and subsequent Calendering.

(60) FIG. 13 demonstrates the overall improvement in TD tensile strength of a dry process microporous membrane produced using the inventive process described herein of TD stretching and subsequent Calendering of a ‘MD stretched’ PE/PP/PE microporous membrane. The dry process manufacturing process which is an environmentally green, solvent-free manufacturing process may produce an MD/TD/Calendered PE/PP/PE microporous membrane with a marked increase in TD tensile strength. In at least certain selected embodiments the porous membranes may be MD and TD stretched and/or relaxed sequentially and/or simultaneously. The calendering step may be introduced before or after the stretching steps. The addition of calendering to the MD/TD stretching and/or relaxing of proous films may increase pore tortuosity contributing to an increase in mechanical strength, may reduce the effective porosity to microporous, and/or the like.

(61) FIG. 14 is a plot of the MD tensile strength of PP/PE/PP and PE/PP/PE trilayer microporous membranes using MD stretch only, MD stretching followed by TD stretching, and the inventive process described herein of MD stretching followed by TD stretching and subsequent Calendering. TD stretching is observed to decrease the MD tensile strength of the PP/PE/PP and PE/PP/PE trilayer microporous membranes. However, subsequent calendering of the MD-subsequent TD stretched membranes may show a recovery of a portion of loss in MD tensile strength. More importantly, the calendering step has produced a membrane where the loss of MD tensile strength is offset by the gain in TD tensile strength. The inventive membrane described herein has a more balanced MD tensile strength and TD tensile strength which may be beneficial to the overall performance of the inventive separator in a battery. In addition, the present porosity has been reduced by approximately 40 to 50%. A controlled reduction in percent porosity to a desirable range to achieve excellent battery performance may be produced by the calendering step when it is performed subsequent to the TD stretching step. In at least certain selected embodiments to improve the MD to TD tensile strength balance and improve the mechanical strength by varying hot and cold stretch temperature conditions.

(62) Due to the less than 10 μm thickness achieved by the possibly preferred inventive MD/TD/Calendered process, the PE/PP/PE microporous membrane produced by the process described herein may provide a thin substrate for polymeric-ceramic coating where the substrate may be easier to coat and have improved adhesion. The inventive microporous membrane PE/PP/PE trilayer configuration offers an excellent substrate for polymeric-ceramic coating where the coating may adhere well and also have excellent adhesion to both the separator substrate and to the electrode in a lithium ion rechargeable battery. A thin PE/PP/PE microporous separator membrane that is less than 10 μm in thickness may have an overall thickness ranging from 14 to 17 μm once coated with a coating layer with a thickness ranging from 4 to 7 μm. In at least certain selected embodiments calendered porous films may be more uniform and provide an improved surface for coating.

(63) FIG. 28 is a set of three Scanning Electron Micrograph (SEM) images (A), (B), and (C) of the cross section of two TD stretched precursors (A) and (B) at 3,000× magnification and a calendered product (C) at 3,500× magnification and a very schematic representation of thickness and of tortuosity (pore path) shown in at least one PE layer of each membrane. SEM (A) is a cross section of a biaxially stretched PP/PE/PP trilayer membrane (see FIG. 6). SEM (B) is a cross section of a biaxially stretched PE/PP/PE trilayer membrane (see FIG. 18). SEM (C) is a cross section of a biaxially stretched and calendered PE/PP/PE trilayer membrane (see FIGS. 20 and 21 (B)). If Tortuosity (T) is defined as the Path length through a tortious pore of the membrane (Pltp) divided by the Path length of a straight through pore (Plsp or membrane thickness), then T=1 is a straight through opening, and then typically T is preferably higher than 1 (such as greater than 1, at least 1.5, at least 2.0, at least 2.5, or higher) in a membrane, separator membrane or separator. Typically, a T greater than 1 is desired to help slow or block dendrites, prevent shorts, and perform properly as a lithium battery separator. A membrane T that is too low or too high can cause issues. Hence, too much MD, TD or biaxial stretching could produce some T=1 pores or an average T less than 1.5. This could be an undesirable or too low of a T. And, too little MD, TD or biaxial stretching and/or too much calendering (too high a pressure or compression) could produce some T=10 pores or an average T over 9. This could be an undesirable or too high of a T. A very low T could lead to dendrites or shorts, while a very high T could lead to undesirable high resistance (ER), high Gurley, low conductance, or the like. In accordance with at least selected embodiments, the Tortuosity or T should be over 1, preferably at least 1.5, more preferably at least 2.0, and most preferably at least 2.5, and may be in a range from 1.5 to 9.5, or over 1 and less than 10. There are exceptions, such as but not limited to, the membrane T should be higher than 1 if not using gel polymer that fills the pores or if the pores are not very tiny (nano) pores (0.001 μm or less) or if the coating on the membrane does not provide an effective T over 1.

(64) FIG. 29 is a schematic surface diagram showing the spreading apart of lamellae to form micropores in a typical MD stretch dry process polyolefin microporous membrane (microporous film). The pores are more slit like MD oriented rectangles (see FIG. 4). In FIG. 29, discrete elongate openings between adjacent lamellae include a plurality of slit like micropores (a small group of slit like pores) defined by the lamellae and bridging structures or fibrils with the lamellae extending in the transverse direction (TD) and the fibrils extending between lamellae in the machine direction (MD) in the typical MD stretch dry process or Celgard process polyolefin membranes. Similar structures can be evident in certain wet process MD stretched polyolefin membranes.

(65) The inventive biaxially stretched and calendered (compressed) membrane of FIG. 19 differs from the typical MD only stretched membrane of FIG. 29. One looking at FIGS. 19 and 29 readily see many differences. The membrane of FIG. 19 has been biaxially stretched and then calendered (compressed). Biaxial stretching creates a precursor membrane structure (such as shown in FIG. 17) quite different and unique as compared to the MD only stretched membrane of FIG. 29. The FIG. 17 membrane is an open, fairly regular or ordered net like structure with thin lamellae, TD elongated groups of pores, some broken or missing fibrils, and the like. When the FIG. 17 precursor membrane is calendered, the open net like structure is compressed, the lamella are collapsed on top of each other in the Z direction, at least the surface lamellae and fibrils are flattened, at least some of the adjacent lamellae at or near the surface are stacked or shingled, and less regular, less ordered, more random, densified lamellar skeletal structure with TD elongated large groups of pores (some without fibrils, some with broken fibrils, some with multiple lamellae, or combinations thereof) are formed (see FIGS. 19 and 30 to 37 of the drawings). The FIG. 19 membrane is one inventive example of a compressed PE/PP/PE trilayer membrane. In this example, the respective PE layers compress more (higher % compression) than the PP layer as the PP layer is less compressible (resists compression). In the FIG. 19 example, some of the groups of pores between lamellae have a much longer TD dimension than MD dimension. For example, some are 4, 4.9, 6.2, 8.5, or 9.1 times longer in the TD than wide in the MD (max TD length/max MD length)(see respective items 4, 2, 1, 3, and 5 in FIG. 31). Some of the pores (or pockets or voids) appear very deep in the Z direction (in the membrane thickness dimension) as fibrils are missing or broken and open to lower pores in a Z direction stack of two or more groups of pores.

(66) A red coloration is added to FIG. 31 to more clearly show the pores (openings, pockets, or voids) defined between the lamellae and the fibrils or bridging structues. Example or selected groups of pores between adjacent lamellae are circled in yellow and labelled 1-5, respectively. Also, in items or areas 1-5 of FIG. 31: 1. The average number of “bridging structures” or fibrils may=˜18 (18.8) (median is 14); 2. The Average number of “micropores”(pores, openings, voids—shaded red) may=27.5 (median=20); 3. The white lines are 1 μm and most micropores are between about 0.5-1.2 μm in height (in MD) and between about 0.2-0.5 μm in width (in TD); and 4. Lamella are about 0.8-1.0 μm thick (in MD).

(67) Such surface pore dimensions (diameter, length, width) are typically measured in the 2 dimensional X-Y plane at the surface. FIG. 19 is the surface SEM of a calendered or compressed PE layer on one side (Side A) of a compressed three layer polyolefin (PE/PP/PE) membrane. It is contemplated that a similar calendered or compressed PE pore structure would be evident on each side of the compressed three layer (PE/PP/PE) membrane, and that a similar calendered or compressed PE pore structure would be evident on each side of a compressed single or multiple layer PE membrane (such as PE, PE/PE, PE/PE/PE, . . . ) or on the PE side of bilayer or multiple layer membranes with an outer PE layer (such as PE/PP, PE/PP/PP, PE/PE/PP, . . . ). The result pore structure may be more ordered if the PE layer is thinner or less TD or biaxially stretched, or it may be less ordered if the PE layer is thicker or more TD or biaxially stretched. The pores (pockets, openings or voids) may be more shallow if the PE layer is thinner or less TD or biaxially stretched, or may be deeper if the PE layer is thicker or more TD or biaxially stretched.

(68) The desired amount of stretch (MD and/or TD) and/or compression is selected to provide the desired thickness, properties, and performance. Too much compression can result in too high of ER or Gurley (too low permeability) while too much stretch can result in too low of ER or Gurley (too high permeability) and may reduce battery life or performance. As described herein dry process polyolefin membranes can be provided that perform the same as or better than wet process membranes and can provide such performance even if they are thinner than the comparative wet process membrane. Thin, strong, performing dry process PO membranes can facilitate the formation of higher energy or higher energy density cells or batteries.

(69) When stretching and compressing PP layers or membranes that are less elastic, less compressible, and typically having smaller pores than similar PE membranes, one would expect a more ordered pore structure than shown in FIG. 19. Nevertheless, PP dry process porous membranes can be provided that perform the same as or better than wet process membranes and can provide such performance even if they are thinner than the comparative wet process membrane. Thin, strong, performing dry process PP membranes can facilitate the formation of higher energy or higher energy density cells or batteries.

(70) FIG. 30 is a combination of FIGS. 19 and 21 (B) together with a schematic figure of a trilayer membrane or product showing that the Side A surface SEM of FIG. 19 is of the upper surface layer of FIG. 21 (B) and that at least the upper surface of the product has a unique pore structure. FIGS. 19, 20 and 21 (B) are SEMs of a biaxially stretched and calendered PE/PP/PE trilayer membrane. Side A or the surface shown in FIG. 19 is the calendered PE surface. With reference to FIG. 30, the pores of the surface or surface layer (calendered PE layer) tend to be trapezoidal or rectangular with rounded corners with condensed or heavy lamellae across the width in at least the outer or surface PE layer. And they appear less regular or periodic and less open than the pores of FIG. 17.

(71) The micropores formed in the network of lamellas of the outer PE layer of FIGS. 19, 20, 21 (B), and 30 are relatively closed-like structures (see surface view FIG. 19) as the result that the structure of lamellas is pressed or compressed in the thickness direction. The cross sectional view shows some extended micropores in the membrane surface direction (see FIGS. 20, 21 (B), and 30. Also, FIG. 27 Panel 3 (bottom 3 SEMs) may show a similar surface view of micropores formed in the network of lamellas of the outer PP layer that are relatively closed-like structures as the result that the structure of lamellas is pressed or compressed in the thickness direction (with less closed or compressed as PP is less compessible and has smaller pores than PE), and there may be some extended micropores in the membrane surface direction.

(72) Before calendering, the outer PE layer had fish net, regular, light, open elongated oval pores which may be too open, too porous, too light, too weak, too compressible, or combinations thereof. See FIGS. 17 and 18.

(73) The ceramic coating filler or particles may have an average particle size in the range of about 0.001 micron to about 5 microns. In another embodiment, the average particle size of the filler may be in a range of about 0.01 micron to 2 microns. U.S. Pat. No. 6,432,586, which is incorporated herein by reference in its entirety, discloses various ceramic-coated separators. Additionally, U.S. Patent Publication No. 2014/0045033, which is also incorporated herein by reference in its entirety, discloses various ceramic particle-containing polymeric coatings for microporous battery separator membranes.

(74) At least certain embodiments, aspects, or objects of the present application may address the above needs, and/or may provide novel, improved or modified membranes, multilayer membranes, separator membranes, calendered membranes, stretched membranes, stretched and calendered membranes, stretched and calendered dry process membranes, separator membranes, coated membranes, membranes with unique structures, membranes with enhanced performance, membrane separators, battery separators, shutdown separators, and/or batteries or cells including such membranes or separators, and/or methods of making such membranes, separators, cells, and/or batteries, and/or methods of using such membranes, separators, cells, and/or batteries. In accordance with at least selected embodiments, the present application or invention is directed to novel or improved stretched membranes, calendered membranes, stretched and calendered membranes, biaxially stretched membranes, sequentially biaxially stretched membranes, simultaneously biaxially stretched membranes, biaxially stretched and calendered membranes, porous membranes, stretched and calendered dry process membranes, dry process separator membranes, coated dry process membranes, membranes with unique structures, membranes with enhanced performance, single or multilayer membranes, microporous membranes, microporous multilayer membranes, thin calendered membranes, thin and strong calendered membranes, thin, strong and/or high performance calendered membranes, dry process membranes, thin dry process membranes, thin calendered dry process membranes, thin and strong calendered dry process membranes, thin, strong and/or high performance calendered dry process membranes, thin, strong and/or high performance calendered dry process membranes with unique structures and/or characteristics, thin, strong and/or high performance calendered and coated dry process membranes, thin, strong and/or high performance stretched and calendered dry process membranes, thin, strong and/or high performance stretched, calendered and coated dry process membranes, battery separator membranes, battery separators, and/or batteries or cells including such membranes or separators, such stretched, calendered and/or coated membranes or separators, such biaxially stretched and/or calendered membranes or separators, such biaxially stretched and/or coated membranes or separators, or such biaxially stretched, calendered, and/or coated membranes or separators, and/or methods of making such membranes, separators, cells, and/or batteries, and/or methods of using such membranes, separators, cells and/or batteries. In accordance with at least certain embodiments, the present application or invention is directed to novel or improved calendered, single or multilayer membranes, trilayer membranes, inverted trilayer membranes, porous membranes, porous multilayer membranes, trilayer dry process membranes, inverted trilayer dry process membranes, battery separator membranes, battery separators, and/or batteries or cells including such membranes or separators, and/or methods of making such membranes, separators, cells, and/or batteries, and/or methods of using such membranes, separators, cells and/or batteries. In accordance with at least certain selected embodiments, the present application or invention is directed to novel or improved monolayer or multilayer porous membranes or separators. In accordance with at least certain particular selected embodiments, the present application or invention is directed to novel or improved monolayer, multilayer, trilayer, inverted trilayer, porous membranes, porous multilayer membranes, battery separator membranes, and/or battery separators such as a multilayer dry process membrane or separator, a dry process polyolefin membrane or separator, a dry process polyolefin multilayer membrane or separator, and/or a polyethylene/polypropylene/polyethylene microporous membrane or separator which is manufactured using an exemplary inventive process described herein which includes stretching and a subsequent calendering step such as a machine direction stretching followed by transverse direction stretching (with or without machine direction relax) and a subsequent calendering step as a possibly preferred means to reduce the thickness of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, to reduce the percent porosity of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, and/or to improve the strength, properties, and/or performance of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, such as the puncture strength, machine direction and/or transverse direction tensile strength, uniformity, wettability, coatability, runnability, compression, spring back, tortuosity, permeability, thickness, pin removal force, mechanical strength, surface roughness, hot tip hole propagation, and/or combinations thereof, of such a stretched membrane, for example, a multilayer porous membrane, in a controlled manner, and/or to produce a unique structure, pore structure, material, membrane, base film, and/or separator. The inventive process may produce 10 μm or less single or multilayer microporous membranes. The inventive process may produce a 10 μm or less multilayer microporous membrane that is easily coated with polymeric-ceramic coatings, has excellent mechanical strength properties due to its inner polypropylene layer, and/or a thermal shutdown function due to the outer polyethylene layers. The ratio of the thickness of the polypropylene and polyethylene layers in such an inventive multilayer microporous membrane can be tailored to select, optimize, and/or balance strength, properties, and/or performance thereof, such as mechanical strength and thermal shutdown properties.

(75) At least certain embodiments, aspects, or objects of the present application may address the industry problems, issues or needs for stronger, thinner, more open, higher C rate, or higher performance separators, and/or may provide novel, improved or modified single or multilayer dry process battery separator membrane, comprising a microporous multilayer separator membrane comprising a trilayer of polyethylene/polypropylene/polyethylene, wherein the membrane has been machine direction stretched followed by a transverse direction stretching, and subsequently calendered using heat and pressure, and/or where said multilayer microporous membrane comprises a polyolefin that may include a polypropylene, a polyethylene, a blend of polyolefins, a mixture of polyolefins, one or more co-polymers of a polyolefin, and combinations thereof, and/or with a thermal shutdown function, and/or where the ratio of the thickness of polyethylene/polypropylene/polyethylene layers ranges from 0.05/0.90/0.05 to 0.25/0.50/0.25, and/or having a thickness of less than 20 μm, preferably less than 15 μm, more preferably less than 12 μm, more preferably less than 10 μm, and/or where the polyethylene/polypropylene/polyethylene microporous membrane has a percent porosity preferably 20% to 55%, more preferably 30% to 50% and most preferably 35% to 50%, and/or where the polyethylene/polypropylene/polyethylene microporous membrane has a TD tensile strength of greater than 500 kgf/cm.sup.2; a ceramic coated microporous membrane as described above comprising:

(76) a multilayer microporous membrane having a first and a second surface,

(77) a ceramic coating on at least one surface of said multilayer microporous membrane, wherein said ceramic coating comprises ceramic particles and may further include a polymeric binder; a novel, improved or modified process comprising:

(78) extruding a polypropylene to form a nonporous precursor membrane and,

(79) extruding a polyethylene to form a nonporous precursor membrane and,

(80) stacking the polypropylene and polyethylene in a rnultilayer polyethylene/polypropylene/polyethylene configuration and,

(81) annealing the multilayer polyethylene/polypropylene/polyethylene non-porous multilayer membrane and,

(82) machine direction stretching the polyethylene/polypropylene/polyethylene non-porous membrane to form an intermediate uniaxial stretched multilayer microporous membrane and, transverse direction stretching the intermediate uniaxial stretched polyethylene/polypropylene/polyethylene multilayer microporous membrane to form a second intermediate MD and TD stretched polyethylene/polypropylene/polyethylene multilayer microporous membrane and, calendering the second intermediate MD and TD stretched polyethylene/polypropylene/polyethylene multilayer microporous membrane to form a polyethylene/polypropylene/polyethylene multilayer microporous membrane, and/or wherein the calendered MD and TD stretched polyethylene/polypropylene/polyethylene multilayer microporous membrane has a thickness less than 20 μm, preferably, less than 15 μm, more preferably less than 12 μm, and more preferably less than 10 μm; a polyethylene/polypropylene/polyethylene battery separator membrane made according to the above process, where the temperature of calendering is less than 90 deg C.; a novel or improved microporous multilayer battery separator membrane, separators, batteries including such separators, methods of making such membranes, separators, and/or batteries, and/or methods of using such membranes, separators and/or batteries; a multilayer dry process polyethylene/polypropylene/polyethylene microporous separator which is manufactured using the inventive process which includes machine direction stretching followed by transverse direction stretching and a subsequent calendering step as a means to reduce thickness of a multilayer microporous membrane, reduce the percent porosity of a multilayer microporous membrane in a controlled manner and improve transverse direction tensile strength; a thin multilayer microporous membrane that is easily coated with polymeric-ceramic coatings, has excellent mechanical strength properties due to its inner polypropylene layer and a thermal shutdown function due to the outer polyethylene layers; the ratio of the thickness of the polypropylene and polyethylene layers in the inventive multilayer microporous membrane can be tailored to balance mechanical strength and thermal shutdown properties; and/or combinations thereof.

(83) At least certain embodiments, aspects, or objects of the present application or invention may provide novel or improved microporous single or multilayer battery separator membranes, separators, batteries including such membranes or separators, methods of making such membranes, separators, and/or batteries, and/or methods of using such membranes, separators and/or batteries. In accordance with at least certain embodiments, a multilayer dry process polyethylene/polypropylene/polyethylene microporous separator which is manufactured using the inventive process which includes machine direction stretching followed by transverse direction stretching and a subsequent calendering step as a means to reduce the thickness of the multilayer microporous membrane, to reduce the percent porosity of the multilayer microporous membrane in a controlled manner and/or to improve transverse direction tensile strength. In a very particular embodiment, the inventive process produces a thin multilayer microporous membrane that is easily coated with polymeric-ceramic coatings, has excellent mechanical strength properties due to its polypropylene layer or layers and a thermal shutdown function due to its polyethylene layer or layers. The ratio of the thickness of the polypropylene and polyethylene layers in the inventive multilayer microporous membrane can be tailored to balance mechanical strength and thermal shutdown properties.

(84) At least certain embodiments, aspects, or objects of the present application or invention may address the needs for and/or may provide a novel or improved multilayer shutdown microporous membrane that has a thickness less than 10 μm for use as a battery separator and/or as a microporous substrate for polymeric-ceramic based coatings to form a coated battery separator, a multilayer shutdown microporous membrane with a thickness less than 10 μm which may be easily coated with a polymeric-ceramic based coating where the coating has excellent adhesion to the membrane and excellent adhesion to an electrode, a multilayer shutdown microporous membrane with a thickness less than 10 μm which may be coated with a polymeric-ceramic based coating where the coating thickness may be less than 7 μm, a need for a multilayer shutdown microporous membrane with a thickness less than 10 μm which has excellent machine direction (MD) and transverse direction (TD) tensile strength and that can be easily coated with a polymeric-ceramic coating, and/or combinations thereof.

(85) The present application is directed to novel or improved microporous single or multilayer battery separator membranes, membrane separators, or separators, and/or batteries or cells including such membranes or separators, and/or methods of making such membranes, separators, cells, and/or batteries, and/or methods of using such membranes, separators, cells, and/or batteries. In accordance with at least certain embodiments, the present invention is directed to a single layer or multilayer dry process polyolefin microporous membrane, membrane separator or separator (such as PP, PE, PP/PP, PE/PE, PP/PE, PP/PE/PP, PE/PP/PE, PE/PP/PP, PP/PE/PE, PE/PP/PP/PE, PP/PE/PE/PP, PP/PP/PP, PE/PE/PE, PP-PE, PP-PE/PP, PP-PE/PE, PP-PE/PP/PP-PE, PP-PE/PE/PP-PE, or the like) which is manufactured using the inventive process which includes machine direction stretching followed by transverse direction stretching (with or without MD relax, preferably with MD relax, such as with 10-90% MD relax, 20-80% MD relax, 30-70% MD relax, or 40-60% MD relax, or with at least 20% MD relax) and a subsequent calendering step as a means to reduce the thickness of the membrane, reduce the percent porosity of the membrane in a controlled manner and/or to improve transverse direction tensile strength. The inventive process may produce a 10 μm or less thick single layer or multilayer microporous membrane, separator membrane, base film, or separator that is easily coated with polymeric-ceramic coatings, has excellent mechanical strength properties due to its polypropylene layer(s) and/or a thermal shutdown function due to its polyethylene layer(s). The ratio of the thickness of the polypropylene and polyethylene layers in the inventive multilayer microporous membrane can be tailored to balance mechanical strength and thermal shutdown properties.

Test Methods

(86) Thickness

(87) Thickness is measured using the Emveco Microgage 210-A precision micrometer thickness tester according to test procedure ASTM D374. Thickness values are reported in units of micrometers, μm.

(88) Gurley

(89) Gurley is defined as the Japanese Industrial Standard (JIS Gurley) JIS P8117 and is an air permeability test measured using the OHKEN permeability tester. JIS Gurley is the time in seconds required for 100 cc of air to pass through one square inch of film at constant pressure of 4.8 inches of water.

(90) Puncture Strength

(91) Test samples are pre-conditioned to 73.4 deg C. and a relative humidity of 50% for a minimum of 20 minutes. An Instron Model 4442 is used to measure puncture strength of test sample. Thirty measurements are made across the diagonal direction of a 1¼″×40″ continuous sample specimen and averaged. The puncturing needle has a 0.5 mm radius. The rate of descent of the puncturing needle is 25 mm/min. The film is held tight in a clamping device which utilizes an O-ring to securely hold the test sample in place. The diameter of this secured area is 25 mm. The displacement (in mm) of the film that was pierced by the puncturing needle is recorded against the resistance force (in gram force) developed by the tested film. The maximum resistance force is the puncture strength in units of gram force (gf). A load-versus-displacement plot is produced by this test method.

(92) Porosity

(93) The porosity of a microporous film sample is measured using ASTM method D-2873 and is defined as the percent void spaces in a microporous membrane.

(94) TD and MD Tensile Strength

(95) The tensile strength along the Machine direction (MD) and Transverse direction (TD) directions is measured using Instron Model 4201 according to ASTM D-882 method.

(96) Electrical Resistance (ER)

(97) Electrical Resistance is defined as the Resistance value in ohm-cm.sup.2 of a separator filled with electrolyte. The separator resistance is characterized by cutting small pieces of separators from the finished material and then placing them between two blocking electrodes. The separators are saturated with the battery electrolyte with 1.0 M LiPF.sub.6 salt in EC/EMC solvent of 3:7 ratio by volume. The Resistance, R, in Ohms (Ω), of the separator is measured by a 4-probe AC impedance technique. In order to reduce the measurement error on the electrode/separator interface, multiple measurements are needed by adding more layers. Based on the multiple layer measurements, the electric (ionic) resistance, R.sub.s (Ω), of the separator saturated with electrolyte is then calculated by the formula R.sub.s=p.sub.sl/A where p.sub.s is the ionic resistivity of the separator in Ω-cm, A is the electrode area in cm.sup.2 and l is the thickness of the separator in cm. The ratio p.sub.s/A=is the slope calculated for the variation of the separator resistance (ΔR) with multiple layers (Δδ) which is given by slope=p.sub.s/A=ΔR/Δδ.

(98) MD and TD % Elongation

(99) The MD % elongation or the % MD elongation at break is the percentage of extension in the machine direction of a test sample measured at the maximum tensile strength needed to break a sample. The TD % elongation or the % TD elongation at break is the percentage of extension in the transverse direction of a test sample measured at the maximum tensile strength needed to break a sample.

(100) Roughness:

(101) The Nanovea ST400 3D Profilometer utilizing a 12 μm (in diameter) needle to measure the surface characteristics of membranes. Using a non-contact optical line sensor a scan is made and quantified using analysis software.

(102) COF:

(103) Rhesca FPR-2000 Friction Player was used to determine the surface friction coefficient of the membrane.

(104) Hot Tip Hole Propagation Test:

(105) In the Hot tip hole propagation test a hot tip probe at a temperature of 450° C. with a tip diameter of 0.5 mm is touched to the surface of the separator membrane. The hot tip probe approaches the membrane at a speed of 10 mm/minute and is allowed to contact the surface of the separator membrane for a period of 10 seconds. Results are captured using a digital image taken with an optical microscope showing both the shape of the hole formed as a result of the response of the separator membrane to 450° C. hot tip probe and the diameter of the hole in the separator after hot tip probe is removed. Minimal propagation of the hole in the separator membrane from contact with the hot tip probe simulates the desired response of the separator membrane to a localized hot spot which may occur during an internal short circuit in Li-ion cells.

(106) The present invention may be embodied in other forms without departing from the spirit and the essential attributes thereof, and, accordingly, reference should be made to the appended claims, rather than to the foregoing specification, as indicating the scope of the invention. Additionally, the invention illustratively disclosed herein suitably may be practiced in the absence of any element which is not specifically disclosed herein.