A system for controlling a clock rate of a microprocessor which includes a core clock operatively coupled to the processor, the core clock providing the microprocessor with a core clock signal for clocking the processor. A power supply operatively coupled to the microprocessor provides power to the processor. An intelligent clock generating system provides the core clock with at least one clock signal of a plurality of clock signals to be used as the core clock signal, wherein the plurality of clock signals includes a master clock signal and at least one ramped clock signal.

Microprocessors are sophisticated, general purpose logic devices which can be programmed to perform a wide variety of useful control functions in industrial and communications equipment, large scale and medium scale computer peripheral and terminal hardware, automobiles and other transportation media, amusement and educational devices, household appliances and other consumer goods, and the like. Generally, an entire spectrum of microprocessors is available in the commercial marketplace. As the speed of operation increases, the more valuable and more versatile the microprocessor becomes since it is capable of controlling the given operation more efficiently and more accurately, of controlling a greater number of operations simultaneously, and of controlling operations requiring relatively fast response times.
The throughput of any given microprocessor is a function of, among other things, the number of machine cycles required to execute a given set of instructions. In the course of designing any computer system, and in particular a microprocessor, a set of instructions is selected which will provide the anticipated program requirements for the projected market in which the microprocessor system is to be used. The microprocessor, executes each instruction as a sequence of machine cycles, with the more complex instructions consuming a greater number of machine cycles.
The operation of internal circuitry of the microprocessor is synchronized by means of a master clock signal applied to the microprocessor. The master clock signal may actually comprise two or even four clock components/signals (i.e., the microprocessor may be either two-phase or four-phase). During the basic clock cycle known as the machine cycle, a number of internal microprocessor related operations may take place simultaneously including the transfer of digital information from a bus to a register or vice versa, between certain registers, from an address or data buffer to a bus or vice versa, and so forth. Additionally, the individual conductors of a bus may each be set to a predetermined logic level, or the contents of a register may be set to a predetermined logic level.
Sometimes, an internal arrangement is deployed within the information processing unit utilizing a PLL (Phase Lock Loop) circuit which delays the clock signals so that the signals are in specific phase relation with desired clock signals. In other words, instead of the multi-phase clocks, the PLL circuit delivers the clock signals for controlling the logic devices. PLL circuits are usually employed to guarantee duty cycles and phase relationships to an input clock source, and PLLs may be used in microprocessors to multiply an internal clock frequency to a significantly higher internal clock frequency. For example, a typical 100 MHZ microprocessor is usually driven by a 33-66 MHZ external clock which is multiplied via a PLL to increase the clock frequency to 100 MHZ.
Conventional microprocessors can also be controlled by clock signals utilizing semiconductor integrated circuit devices having logic circuits controlled by clock signals such as "A 130 K-Gate CMOS Mainframe Chip Set" ISSCC 87, SESSION VIII,pp. 86-87, 1987 or "A 15MIPS 32b Microprocessor" ISSCC 87, SESSION II, pp. 26-27, 1987. In these microprocessor, an external clock signal input to a pad is formed into an internal clock signal through an input buffer. The clock signal is distributed by a first-stage clock buffer in the form of clock signals, and these signals are further distributed by a second-stage clock buffer in the form of clock signals to control the logic circuit blocks. In this approach, logic circuit blocks which are present throughout the semiconductor integrated circuit device and which are controlled by clock signals are divided into a plurality of blocks and a clock buffer is provided for each of the divided logic circuit blocks to supply a clock signal thereto, thereby enabling a reduction in the load which is driven by each clock buffer.
Numerous technologies and resources have been deployed to advance clocking technology with an emphasis on improving the speed of the microprocessor.
A significant clock related problem with microprocessors is power consumption. Systems for placing the microprocessor in a static or idle state have been developed in order to conserve power consumption. However, if the microprocessor is in an idle state, for example, drawing a minimal amount of power and then suddenly is awakened due to a key stroke or the like, the microprocessor transgresses from minimal speed to full speed almost immediately. This is because the clock signal driving the microprocessor is substantially at full speed when the microprocessor is awakened from an idle state. The current demand of the microprocessor is a function of operating frequency. Accordingly, as the microprocessor speeds rapidly increases from low speed to high speed, current demand by the microprocessor correspondingly increases rapidly.
In order to enable the microprocessor to transition from a minimal power state to a full power state almost instantaneously, large bulk capacitor(s) or complex power supplies are typically required. The large bulk capacitor(s) store sufficient amount of energy such that when the microprocessor is awakened the microprocessor is provided with enough current to sustain operation at full speed until a power supply for the microprocessor can adjust to the change in microprocessor load.
Generally, a microprocessor power supply takes several milliseconds to adjust to a change in microprocessor load. Because the microprocessor typically goes from almost zero power to almost full power in less than or equal to 10 nanoseconds, a capacitor which discharges rapidly is needed in order to sustain power to the microprocessor until the power supply can take over. In order for the capacitor to be able to discharge so rapidly and provide sufficient power for several milliseconds (i.e., the time needed for the power supply to adjust), the capacitor typically is relatively large in size. Attempts have been made to remedy this problem to some extent by making the power supplies more intelligent. However, since the power demand for relatively instantaneous powering of the microprocessor is high, the power supply cannot circumvent the need for the employment of large bulk capacitors without being unduly costly and complicated. A problem with having to use a large bulk capacitor or several smaller capacitors in cascade is that they occupy valuable space which is highly undesirable in this age of miniaturization. Furthermore, electromagnetic fields generated by the capacitor(s) may cause interference and hinder microprocessor performance including that related to speed.
In view of the above, there is a need in the art for a system and method which controls a clock rate of a microprocessor in order to control startup power requirements and avoid the need for large bulk capacitors and/or complex power supplies.

System and method to control microprocessor startup to reduce power supply bulk capacitance needs


A co-extruded sheet made from olefin polymer materials includes (1) at least one outer layer of (a) a propylene polymer having a melt flow rate of 0.5-15 dg/min, or a graft copolymer comprising a backbone of a propylene polymer material, to which is graft polymerized a vinyl monomer, and (b) a nucleating agent having a melting point greater than 265xc2x0 C. and (2) another layer made from (a) about 5% to about 50% of a high melt strength propylene homopolymer or copolymer, and/or about 5% to about 40% of chopped glass fibers, (b). optionally about 5% to about 40% of an inorganic filler, (c) about 2% to about 50% of an olefin polymer composition, and (d) optionally about 5% to about 70% of one or more other olefin polymer materials. When the second layer is reinforced with glass fibers, the stiffness of the sheet is increased while maintaining impact strength. The sheet has high surface gloss and good chemical resistance, and can be thermoformed using a melt phase thermoforming process wherein the surface temperature of the nucleated propylene polymer layer is from at least 310xc2x0 F.

This invention relates to co-extruded sheets made from olefin polymer materials.
Structural parts, especially large structural parts, have typically been made from an acrylonitrile/butadiene/styrene rubber (ABS). When weatherability is required, a laminate of ABS and a layer of acrylonitrile/styrene/acrylic resin (ASA) or an acrylic resin is used. These materials have only adequate weatherability, poor chemical resistance, and a high density, which is a disadvantage when used in applications such as, for example, co-extruded profiles; boat hulls and boat decks as well as boat engine covers, consoles, and hatches; indoor and outdoor whirlpool tubs or hot tubs; pick-up truck caps, and body parts for golf carts, all-terrain vehicles, lawn mowers and lawn tractors, and agricultural equipment.
European Patent Application 873,862 discloses co-extruded laminates comprising at least one layer of a graft copolymer made from a propylene polymer material onto which is graft polymerized acrylic and/or styrenic monomers, and at least one other layer comprising one or more polyolefin materials, which may include a high melt strength propylene polymer material. These laminates are characterized by better weather resistance, better chemical resistance, greater toughness, and better scratch and mar resistance than materials available at that time for making large thermoformed structural parts.
Glass fibers have been used to reinforce various polyolefin materials. For example, U.S. Pat. No. 5,030,682 discloses a glass fiber reinforced polyolefin resin composition consisting essentially of (a) 15-80% polypropylene-1, (b) 20-60% polybutene-1, (c) 5-60% glass fiber, (d) 0-5 parts by weight of polyolefin modified with an unsaturated carboxylic acid or unsaturated carboxylic acid derivative per 100 parts of the resin composition, and (e) 0.01-3 parts by weight of a crystal nucleating agent per 100 parts of the resin composition. The composition can be molded to make products having superior surface smoothness, superior heat resistance, and improved mechanical properties.
However, there is still a need for polymer materials having even greater melt strength that will produce thermoformed parts that have an even higher surface gloss after thermoforming than currently available materials. There is also a need for thermoformed parts with significantly increased flexural modulus and good impact strength.
The co-extruded sheet of the present invention comprises:
(1) at least one outer layer comprising (a) a propylene polymer material selected from the group consisting of (i) a propylene homopolymer or a copolymer of propylene and ethylene or a 4-8 C alpha-olefin, both having a melt flow rate (MFR) of 0.5 to 15 dg/min, wherein the polymerized ethylene or polymerized alpha-olefin content of the copolymer is not greater than 20%, and (ii) a graft copolymer comprising a backbone of a propylene polymer material, having graft polymerized thereto polymerized monomers selected from the group consisting of: at least one acrylic monomer, (II) at least one styrenic monomer, and (III) mixtures of (I) and (II), and (b) about 0.15% to about 0.70% of a nucleating agent having a melting point greater than 265xc2x0 C. when the propylene polymer material is (i) or about 0.5% to about 1.5% of a nucleating agent having a melting point greater than 265xc2x0 C. when the propylene polymer material is (ii), and
(2) another layer comprising:
(a) a material selected from the group consisting of (i) about 5% to about 50% of a propylene polymer having strain hardening elongational viscosity selected from the group consisting of (I) a propylene homopolymer and (II) a copolymer of propylene and ethylene or a 4-10 C alpha-olefin, provided that when the olefin is ethylene, the maximum polymerized ethylene content is 5%, and when the olefin is a 4-10 C alpha-olefin, the maximum polymerized content thereof is 20%, (ii) about 5% to about 40% of chopped glass fibers having a maximum length of xc2xd inch, and (iii) a mixture of (i) and (ii),
(b) optionally about 5% to about 40% of an inorganic filler, the total amount of chopped glass fibers plus inorganic filler, when present, being not greater than 50%,
(c) about 2% to about 50% of an olefin polymer composition comprising
(i) about 10 parts to about 60 parts by weight of a crystalline propylene homopolymer having an isotactic index greater than 80, or a crystalline copolymer from monomers selected from the group consisting of (a) propylene and ethylene, (b) propylene, ethylene and a C4-C8 xcex1-olefin, and (c) propylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content of more than 85% by weight and an isotactic index greater than 85;
(ii) about 5 parts to about 25 parts by weight of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature; and
(iii) about 30 parts to about 70 parts by weight of an elastomeric copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene, and a C4-C8 xcex2-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% by weight of a polymerized diene, and containing less than 70% by weight of polymerized ethylene and being soluble in xylene at ambient temperature and having an intrinsic viscosity measured in decahydronaphthalene at 135xc2x0 C. of about 1.5 to about 4.0 dl/g;
the total of (ii) and (iii), based on the total olefin polymer composition being from about 50% to about 90%, and the weight ratio of (ii)/(iii) being less than 0.4, wherein the composition is prepared by polymerization in at least two stages and has a flexural modulus of less than 150 MPa; and
(d) optionally about 5% to about 70% of at least one propylene polymer material selected from the group consisting of:
(i) a crystalline homopolymer of propylene having an isotactic index greater than 80;
(ii) a crystalline copolymer of propylene and an olefin selected from the group consisting of ethylene and C4-C10 xcex1-olefins, provided that when the olefin is ethylene, the maximum polymerized ethylene content is 10% by weight, and when the olefin is a C4-C10 xcex1-olefin, the maximum polymerized content thereof is 20% by weight, the copolymer having an isotactic index greater than 85;
(iii) a crystalline terpolymer of propylene and two olefins selected from the group consisting of ethylene and C4-C8 xcex1-olefins, provided that the maximum polymerized C4-C8 xcex1-olefin content is 20% by weight, and, when ethylene is one of the olefins, the maximum polymerized ethylene content is 5% by weight, the terpolymer having an isotactic index greater than 85;
(iv) a thermoplastic olefin comprising:
(1) about 10% to about 60% of a propylene homopolymer having an isotactic index greater than 80, or a crystalline copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene, and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content greater than 85% and an isotactic index of greater than 85%;
(2) about 20% to about 60% of an amorphous copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% of a polymerized diene, and containing less than 70% polymerized ethylene and being soluble in xylene at ambient temperature; and
(3) about 3% to about 40% of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature,
wherein the composition has a flexural modulus of greater than 150 but less than 1200 MPa;
(v) a heterophasic polyolefin composition comprising:
(1) about 30% to about 98% of a polymeric material selected from the group consisting of a propylene homopolymer having an isotactic index greater than 90, and a crystalline copolymer having an isotactic index greater than 85 of propylene and at least one xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C6 alkyl group, the polymerized xcex1-olefin being less than 10% of the copolymer when R is H and being less than 20% when R is a C2-C6 alkyl group or a combination thereof with R=H, and
(2) about 2% to about 70% of an elastomeric copolymer of propylene and an xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C8 alkyl group, the polymerized xcex1-olefin being about 45% to about 75% of the elastomeric copolymer, and about 10% to about 40% of the elastomeric copolymer being insoluble in xylene at ambient temperature, or an elastomeric copolymer of ethylene and a C4-C8 xcex1-olefin, having a polymerized xcex1-olefin content of about 15% to about 60%, and
(vi) a graft copolymer comprising a backbone of a propylene polymer material, having graft polymerized thereto polymerized monomers selected from the group consisting of (I) at least one acrylic monomer, (II) at least one styrenic monomer, and (III) mixtures of (I) and (II),
wherein (a)+(b)+(c)+(d)=100%, and
wherein layer (1) comprises about 5% to about 60% of the total thickness of the sheet.
The process of this invention for making a co-extruded sheet comprises co-extruding a multi-layer sheet comprising:
(1) at least one outer layer comprising (a) a propylene polymer material selected from the group consisting of (i) a propylene homopolymer or a copolymer of propylene and ethylene or a 4-8 C alpha-olefin, both having a melt flow rate of 0.5 to 15 dg/min, wherein the polymerized ethylene or polymerized alpha-olefin content of the copolymer is not greater than 20%, and (ii) a graft copolymer comprising a backbone of a propylene polymer material having graft polymerized thereto polymerized monomers selected from the group consisting of (I) at least one acrylic monomer, (II) at least one styrenic monomer, and (III) mixtures of (I) and (II), and (b) about 0.15% to about 0.70% of a nucleating agent having a melting point greater than 265xc2x0 C. when the propylene polymer material is (i) or about 0.5% to about 1.5% of a nucleating agent having a melting point greater than 265xc2x0 C. when the propylene polymer material is (ii), and
(2) another layer comprising:
(a) a material selected from the group consisting of (i) about 5% to about 50% of a propylene polymer having strain hardening elongational viscosity selected from the group consisting of (I) a propylene homopolymer and (II) a copolymer of propylene and ethylene or a 4-10 C alpha-olefin, provided that when the olefin is ethylene, the maximum polymerized ethylene content is 5%, and when the olefin is a 4-10 C alpha-olefin, the maximum polymerized content thereof is 20%, (ii) about 5% to about 40% of chopped glass fibers having a maximum length of xc2xd inch, and (ii) a mixture of (i) and (ii),
(b) optionally about 5% to about 40% of an inorganic filler, the total amount of chopped glass fibers and inorganic filler, when present, being not greater than 50%,
(c) about 2% to about 50% of an olefin polymer composition comprising
(i) about 10 parts to about 60 parts by weight of a crystalline propylene homopolymer having an isotactic index greater than 80, or a crystalline copolymer from monomers selected from the group consisting of (1) propylene and ethylene, (2) propylene, ethylene and a C4-C8 xcex1-olefin, and (3) propylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content of more than 85% by weight and an isotactic index greater than 85;
(ii) about 5 parts to about 25 parts by weight of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature; and
(iii) about 30 parts to about 70 parts by weight of an elastomeric copolymer from monomers selected from the group consisting of (1) ethylene and propylene, (2) ethylene, propylene, and a C4-C8 xcex1-olefin, and (3) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% by weight of a polymerized diene, and containing less than 70% by weight of polymerized ethylene and being soluble in xylene at ambient temperature and having an intrinsic viscosity measured in decahydronaphthalene at 135xc2x0 C. of about 1.5 to about 4.0 dl/g;
the total of (ii) and (iii), based on the total olefin polymer composition being from about 50% to about 90%, and the weight ratio of (ii)/(iii) being less than 0.4, wherein the composition is prepared by polymerization in at least two stages and has a flexural modulus of less than 150 MPa; and
(d) optionally about 5% to about 70% of at least one propylene polymer material selected from the group consisting of:
(i) a crystalline homopolymer of propylene having an isotactic index greater than 80;
(ii) a crystalline copolymer of propylene and an olefin selected from the group consisting of ethylene and C4-C10 xcex1-olefins, provided that when the olefin is ethylene, the maximum polymerized ethylene content is 10% by weight, and when the olefin is a C4-C10 xcex1-olefin, the maximum polymerized content thereof is 20% by weight, the copolymer having an isotactic index greater than 85;
(iii) a crystalline terpolymer of propylene and two olefins selected from the group consisting of ethylene and C4-C8 xcex1-olefins, provided that the maximum polymerized C4-C8 xcex1-olefin content is 20% by weight, and, when ethylene is one of the olefins, the maximum polymerized ethylene content is 5% by weight, the terpolymer having an isotactic index greater than 85;
(iv) a thermoplastic olefin comprising:
(1) about 10% to about 60% of a propylene homopolymer having an isotactic index greater than 80, or a crystalline copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene, and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content greater than 85% and an isotactic index of greater than 85%;
(2) about 20% to about 60% of an amorphous copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% of a polymerized diene, and containing less than 70% polymerized ethylene and being soluble in xylene at ambient temperature; and
(3) about 3% to about 40% of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature,
wherein the composition has a flexural modulus of greater than 150 but less than 1200 MPa;
(v) a heterophasic polyolefin composition comprising:
(1) about 30% to about 98% of a polymeric material selected from the group consisting of a propylene homopolymer having an isotactic index greater than 90, and a crystalline copolymer having an isotactic index greater than 85 of propylene and at least one xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C6 alkyl group, the polymerized xcex1-olefin being less than 10% of the copolymer when R is H and being less than 20% when R is a C2-C6 alkyl group or a combination thereof with R=H, and
(2) about 2% to about 70% of an elastomeric copolymer of propylene and an xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C8 alkyl group, the polymerized xcex1-olefin being about 45% to about 75% of the elastomeric copolymer, and about 10% to about 40% of the elastomeric copolymer being insoluble in xylene at ambient temperature, or an elastomeric copolymer of ethylene and a C4-C8 xcex1-olefin, having a polymerized xcex1-olefin content of about 15% to about 60%, and
(vi) a graft copolymer comprising a backbone of a propylene polymer material having graft polymerized thereto polymerized monomers selected from the group consisting of (I) at least one acrylic monomer, (II) at least one styrenic monomer, and (III) mixtures of (I) and (II),
wherein (a)+(b)+(c)+(d)=100%, and
wherein layer (1) comprises about 5% to about 60% of the total thickness of the sheet, at a polymer melt temperature of 230-255xc2x0 C. as it comes from the extruder die.
The co-extruded sheets of this invention have a highly crystalline hard surface with a high gloss after melt phase thermoforming and good chemical resistance. Large thermoformed structural parts with a deep draw and good part definition can be made from these sheets. A number of different materials can be selected for the optional fourth component of the second layer, making it possible to design a wide variety of materials with whatever combination of properties is desired in the finished product. This combination of properties is not achievable when using a single layer sheet.
When glass fibers are present in layer (2), the co-extruded sheets have a significantly higher flexural modulus than sheets without the glass reinforcement, while maintaining good impact strength.
Composite materials comprising at least one layer of this laminate attached to a low density polyolefin foam layer are another embodiment of this invention.
The propylene polymer material (a)(i) that is used in outer layer (1) of the co-extruded sheet of this invention can be a propylene homopolymer or a copolymer of propylene and ethylene or a 4-8 C alpha-olefin, wherein the total amount of polymerized ethylene or polymerized alpha-olefin is not greater than 20%. The homopolymer or copolymer has a melt flow rate of 0.5 to 15 dg/min, preferably about 1.0 to about 4.0 dg/min.
Any propylene homopolymer or copolymer of the specified type having this melt flow rate can be used. However, polymers obtained by visbreaking a polymer having a lower MFR, i.e., subjecting the polymer to chain scission, are preferred. This visbreaking process not only lowers the molecular weight and raises the MFR of the polymers, but it also leads to a narrowing of the molecular weight distribution. Generally speaking, higher molecular weight leads to better physical properties but poorer processing properties. Conversely, lower molecular weight leads to poorer physical properties but better processing properties. A low molecular weight polymer with narrow molecular weight distribution gives both good physical and processing properties in many fabricated articles. Therefore it is a common procedure to polymerize to a higher molecular weight than desired for the final application, and then to visbreak to the desired molecular weight.
In commercial practice visbreaking is generally achieved by the addition of a prodegradant to the polymer before pelletization. Alternatively, the polymer and the prodegradant can be mixed in the extruder while heating. A prodegradant is a substance that promotes chain scission when mixed with the polymer, which is then heated under extrusion conditions. The prodegradants used in current commercial practice are mainly alkyl hydroperoxides or dialkyl peroxides. These materials initiate a free radical chain reaction at elevated temperatures, resulting in scission of the propylene polymer molecules. Alternatively, visbreaking can be accomplished by using shear, or a combination of shear and temperature, without the use of a prodegradant.
The propylene polymer material (a) that is used in outer layer (1) of the co-extruded sheet of this invention can also be a graft copolymer comprising a backbone of a propylene polymer material having graft polymerized thereto monomers selected from the group consisting of: (I) at least one acrylic monomer, (II) at least one styrenic monomer, and (III) mixtures of (I) and (II).
The propylene polymer material that is used as the backbone of the graft copolymer can be:
(1) a homopolymer of propylene having an isotactic index greater than 80, preferably about 85 to about 99;
(2) a copolymer of propylene and an olefin selected from the group consisting of ethylene and 4-10 C alpha-olefins, provided that when the olefin is ethylene, the maximum polymerized ethylene content is about 10%, preferably about 4%, and when the olefin is a 4-10 C alpha-olefin, the maximum polymerized content thereof is about 20% by weight, preferably about 16%, the copolymer having an isotactic index greater than 85;
(3) a terpolymer of propylene and two olefins selected from the group consisting of ethylene and 4-8 C alpha-olefins, provided that the maximum polymerized 4-8 C alpha-olefin content is 20% by weight, preferably about 16%, and, when ethylene is one of the olefins, the maximum polymerized ethylene content is 5% by weight, preferably about 4%, the terpolymer having an isotactic index greater than 85;
(4) an olefin polymer composition comprising:
(a) about 10% to about 60% by weight, preferably about 15% to about 55%, of a propylene homopolymer having an isotactic index greater than 80, preferably about 85 to about 98, or a copolymer of monomers selected from the group consisting of (i) propylene and ethylene, (ii) propylene, ethylene and a 4-8 C alpha-olefin, and (iii) propylene and a 4-8 C alpha-olefin; the copolymer having a polymerized propylene content of more than 85% by weight, preferably about 90% to about 99%, and an isotactic index greater than 85;
(b) about 5% to about 25% by weight, preferably about 5% to about 20%, of a copolymer of ethylene and propylene or a 4-8 C alpha-olefin that is insoluble in xylene at ambient temperature; and
(c) about 30% to about 70% by weight, preferably about 40% to about 65%, of an elastomeric copolymer of monomers selected from the group consisting of (i) ethylene and propylene, (ii) ethylene, propylene, and a 4-8 C alpha-olefin, and (iii) ethylene and a 4-8 C alpha-olefin, the copolymer optionally containing about 0.5% to about 10% by weight of a polymerized diene and containing less than 70% by weight, preferably about 10% to about 60%, most preferably about 12% to about 55%, of polymerized ethylene and being soluble in xylene at ambient temperature and having an intrinsic viscosity, measured in decahydronaphthalene at 135xc2x0 C., of about 1.5 to about 4.0 dl/g,
wherein the total amount of (b) and (c), based on the total olefin polymer composition, is about 50% to about 90%, the weight ratio of (b)/(c) is less than 0.4, preferably 0.1 to 0.3, and the composition is prepared by polymerization in at least two stages and has a flexural modulus of less than 150 MPa; or
(5) a thermoplastic olefin comprising:
(a) about 10% to about 60%, preferably about 20% to about 50%, of a propylene homopolymer having an isotactic index greater than 80, or a copolymer of monomers selected from the group consisting of (i) ethylene and propylene, (ii) ethylene, propylene and a 4-8 C alpha-olefin, and (iii) ethylene and a 4-8 C alpha-olefin, the copolymer having a polymerized propylene content greater than 85% and an isotactic index of greater than 85;
(b) about 20% to about 60%, preferably about 30% to about 50%, of an amorphous copolymer from monomers selected from the group consisting of (i) ethylene and propylene, (ii) ethylene, propylene, and a 4-8 C alpha-olefin, and (iii) ethylene and a 4-8 C alpha-olefin, the copolymer optionally containing about 0.5% to about 10% of a polymerized diene, and containing less than 70% polymerized ethylene and being soluble in xylene at ambient temperature; and
(c) about 3% to about 40%, preferably about 10% to about 20%, of a copolymer of ethylene and propylene or a 4-8 C alpha-olefin that is insoluble in xylene at ambient temperature,
wherein the thermoplastic olefin has a flexural modulus of greater than 150 but less than 1200 MPa, preferably about 200 to about 1100 MPa, and most preferably about 200 to about 1000 MPa.
Room or ambient temperature is xcx9c25xc2x0 C.
The 4-8 C alpha-olefins useful in the preparation of (4) and (5) include, for example, butene-1, pentene-1; hexene-1; 4-methyl-1-pentene, and octene-1.
The diene, when present, is typically a butadiene; 1,4-hexadiene; 1,5-hexadiene, or ethylidenenorbornene.
Propylene polymer materials (4) and (5) can be prepared by polymerization in at least two stages, where in the first stage the propylene; propylene and ethylene; propylene and an alpha-olefin, or propylene, ethylene and an alpha-olefin are polymerized to form component (a) of (4) or (5), and in the following stages the mixtures of ethylene and propylene; ethylene and the alpha-olefin, or ethylene, propylene and the alpha-olefin, and optionally a diene, are polymerized in the presence of (a) to form components (b) and (c) of (4) or (5).
The polymerization can be conducted in liquid phase, gas phase, or liquid-gas phase using separate reactors, all of which can be done either by batch or continuously. For example, it is possible to carry out the polymerization of component (a) using liquid propylene as a diluent, and the polymerization of components (b) and (c) in gas phase, without intermediate stages except for the partial degassing of the propylene. All gas phase is the preferred method.
The preparation of propylene polymer material (4) is described in more detail in U.S. Pat. Nos. 5,212,246 and 5,409,992, which are incorporated herein by reference. The preparation of propylene polymer material (5) is described in more detail in U.S. Pat. Nos. 5,302,454 and 5,409,992, which are incorporated herein by reference.
Propylene homopolymer is the preferred propylene polymer backbone material.
The acrylic monomers that can be graft polymerized onto the propylene polymer material backbone include, for example, acrylic acid; acrylate esters, such as the methyl, ethyl, hydroxyethyl, 2-ethylhexyl, and butyl acrylate esters; methacrylic acid, and methacrylate esters such as the methyl, ethyl, butyl, benzyl, phenylethyl, phenoxyethyl, epoxypropyl, hydroxypropyl methacrylate esters, and mixtures thereof.
The styrenic monomers that can be graft polymerized onto the propylene polymer material backbone include styrene and alkyl or alkoxy ring-substituted styrenes where the alkyl or alkoxy group is a 1-4 C linear or branched alkyl or alkoxy group, and mixtures thereof.
When a mixture of acrylic and styrenic monomers is used, the ratio of acrylic to styrenic monomers can be about 95/5 to about 5/95.
The polymerized monomers comprise about 10 to about 120 parts per hundred parts of the propylene polymer material, preferably about 30 to about 95 pph.
During the graft polymerization, the monomers also polymerize to form a certain amount of free or ungrafted polymer. The morphology of the graft copolymer is such that the propylene polymer material is a continuous or matrix phase, and the polymerized monomer, both grafted and ungrafted, is a dispersed phase.
The graft copolymer can be made according to any one of various methods. One of these methods involves forming active grafting sites on the propylene polymer material by treatment with a peroxide or other chemical compound that is a free radical polymerization initiator, or by irradiation with high energy ionizing radiation. The free radicals produced on the polymer as a result of the chemical or irradiation treatment form the active grafting sites on the polymer and initiate the polymerization of the monomers at these sites. Graft copolymers produced by peroxide-inlitiated grafting methods are preferred.
Preparation of graft copolymers by contacting the polypropylene with a free radical polymerization initiator such as an organic peroxide and a vinyl monomer is described in more detail in U.S. Pat. No. 5,140,074, which is incorporated herein by reference. Preparation of graft copolymers by irradiating an olefin polymer and then treating with a vinyl monomer is described in more detail in U.S. Pat. No. 5,411,994, which is incorporated herein by reference.
When the propylene polymer material in layer (1) is a graft copolymer, the composition can also contain about 2% to about 30%, preferably about 5% to about 30%, based on the total weight of the composition, of one or more rubber components, and/or about 15% to about 50%, preferably about 40% to about 50%, based on the total weight of the composition, of a broad molecular weight distribution propylene polymer material.
The rubber component is selected from one or more of the group consisting of (i) an olefin copolymer rubber, (ii) a monoalkenyl aromatic hydrocarbon-conjugated diene block copolymer, and (iii) a core-shell rubber. Any of these rubber components can have acid or anhydride functionality or can be free of these functional groups. The preferred rubber components are (i) or (ii), either alone or in combination.
Suitable olefin copolymer rubbers include, for example, saturated olefin copolymer rubbers such as ethylene/propylene monomer rubbers (EPM), ethylene/octene-1, and ethylene/butene-1rubbers, and unsaturated olefin copolymer rubbers such as ethylene/propylene/diene monomer rubbers (EPDM). The preferred olefin copolymer rubbers are ethylene/propylene, ethylene/butene-1, and ethylene/octene-1copolymers.
The monoalkenyl aromatic hydrocarbon-conjugated diene block copolymer can be a thermoplastic elastomer of the A-B (or diblock) structure, the linear A-B-A (or triblock) structure, the radial (A-B)n type where n=3-20%, or a combination of these structure types, wherein each A block is a monoalkenyl aromatic hydrocarbon polymer block, and each B block is an unsaturated rubber block. Various grades of copolymers of this type are commercially available. The grades differ in structure, molecular weight of the mid and end blocks, and the ratio of monoalkenyl aromatic hydrocarbon to rubber. The block copolymer can also be hydrogenated. Typical monoalkenyl aromatic hydrocarbon monomers are styrene, ring-substituted 1-4 C linear or branched alkyl styrenes, and vinyltoluene. Styrene is preferred. Suitable conjugated dienes include, for example, butadiene and isoprene. Preferred block copolymers are hydrogenated styrene/ethylene-butene-1/styrene triblock copolymers.
The weight average molecular weight (Mw) of the block copolymers generally will be in the range of about 45,000 to about 260,000 g/mole, average molecular weights in the range of about 50,000 to about 125,000 g/mole being preferred on the basis that they produce compositions having the best balance of impact strength and stiffness. Also, while block copolymers having unsaturated as well as saturated rubber blocks can be used, copolymers having saturated rubber blocks are preferred, also on the basis of the impact/stiffness balance of the compositions containing them. The weight ratio of monoalkenyl aromatic hydrocarbon to conjugated diene rubber in the block copolymer is in the range of about 5/95 to about 50/50, preferably about 10/90 to about 40/60.
The core-shell rubber components comprise small particles of a crosslinked rubber phase surrounded by a compatibilizing shell, normally a glassy polymer or copolymer. The core is typically a diene rubber such as butadiene or isoprene rubber, or a polyacrylate. The shell is typically a polymer of two or more monomers selected from styrene, methyl methacrylate, and acrylonitrile. Particularly preferred core-shell rubbers have a polyacrylate core.
Suitable impact modifiers include, for example, Engage 8150 or Engage 8200 ethylene/octene-1copolymers commercially available from DuPont-Dow Elastomers; EPM 306P ethylene/propylene copolymer, commercially available from the Polysar Rubber Division of Miles, Incorporated; and Kraton RP6912 styrene/ethylene-propylene/styrene triblock copolymer. rubber and Kraton FG1901X styrene/ethylene-butene-1/styrene triblock copolymer rubber modified with maleic anhydride, commercially available from Shell Chemical Company.
Another optional ingredient is a broad molecular weight distribution propylene polymer material (BMWD PP) having a Mw/Mn of about 5 to about 60, preferably about 5 to about 40; a melt flow rate of about 0.5 to about 50, preferably about 1 to about 30 g/10 min, and xylene insolubles at 25xc2x0 C. of greater than or equal to 94%, preferably greater than or equal to 96%, and most preferably greater than or equal to 98%. The propylene polymer material having a broad molecular weight distribution can be a homopolymer of propylene or an ethylene/propylene rubber impact-modified homopolymer of propylene, wherein the propylene homopolymer has a broad molecular weight distribution.
The BMWD PP can be prepared by sequential polymerization in at least two stages, in the presence of a Ziegler-Natta catalyst supported on magnesium halide in active form. The polymerization process occurs in separate and consecutive stages, and in each stage polymerization takes place in the presence of the polymer and the catalyst from the preceding stage.
The polymerization process can be carried out in a batch or in a continuous mode according to known techniques, operating in liquid phase in the presence or not of an inert diluent, or in gas phase, or liquid-gas phase, preferably in gas phase. The preparation of the BMWD PP is described in more detail in U.S. Pat. No. 5,286,791, which is incorporated herein by reference.
When the propylene polymer material in layer (1) is a propylene homopolymer or copolymer, the nucleating agent having a melting point of greater than 265xc2x0 C. is present in an amount of about 0.15% to about 0.70%, preferably about 0.2% to about 0.4%. When the propylene polymer material is a graft copolymer, the nucleating agent having a melting point of greater than 265xc2x0 C. is present in an amount of about 0.5% to about 1.5%, preferably about 0.7% to about 1.3%. Bis(3,4-dimethylbenzylidene) sorbitol is preferred because of its good temperature resistance during thermoforming, i.e., it has a melting point of 275xc2x0 C.
The nucleated polypropylene layer (1) is about 5% to about 60% of the total thickness of the laminate.
Layer (2) of the laminate of this invention comprises:
(a) a material selected from the group consisting of (i) about 5% to about 50%, preferably about 15% to about 30%, of a propylene polymer having strain hardening elongational viscosity selected from the group consisting of (i) a propylene homopolymer and (ii) a copolymer of propylene and ethylene or a 4-10 C alpha-olefin, provided that when the olefin is ethylene, the maximum polymerized ethylene content is about 5%, and when the olefin is a 4-10 C alpha-olefin, the maximum polymerized content thereof is 20%, (ii) about 5% to about 40%, preferably about 15% to about 25%, of chopped glass fibers having a maximum length of xc2xd inch, and (ii) a mixture of (i) and (ii),
(b) optionally about 5% to about 40%, preferably about 10% to about 30%, of an inorganic filler, the total amount of chopped glass fibers plus inorganic filler, when present, being not greater than 50%,
(c) about 2% to about 50%, preferably about 10% to about 30%, of an olefin polymer composition comprising
(i) about 10 parts to about 60 parts by weight, preferably about 15 parts to about 55 parts, of a crystalline propylene homopolymer having an isotactic index greater than 80, preferably about 85 to about 98, or a crystalline copolymer from monomers selected from the group consisting of (1) propylene and ethylene, (2) propylene, ethylene and a C4-C8 xcex1-olefin, and (3) propylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content of more than 85% by weight, preferably about 90% to about 99%, and an isotactic index greater than 85;
(ii) about 5 parts to about 25 parts by weight, preferably about 5 parts to about 20 parts, of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature; and
(ii) about 30 parts to about 70 parts by weight, preferably about 20 parts to about 65 parts, of an elastomeric copolymer from monomers selected from the group consisting of (1) ethylene and propylene, (2) ethylene, propylene, and a C4-C8 xcex1-olefin, and (3) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% by weight of a polymerized diene, and containing less than 70% by weight, preferably about 10% to about 60%, most preferably about 12% to about 55%, of polymerized ethylene and being soluble in xylene at ambient temperature and having an intrinsic viscosity measured in decahydronaphthalene at 135xc2x0 C. of about 1.5 to about 4.0 dl/g;
the total of (ii) and (iii), based on the total olefin polymer composition being from about 50% to about 90%, and the weight ratio of (ii)/(iii) being less than 0.4, preferably 0.1 to 0.3, wherein the composition is prepared by polymerization in at least two stages and has a flexural modulus of less than 150 MPa; and
(d) optionally about 5% to about 70%, preferably about 30% to about 60%, of at least one propylene polymer material selected from the group consisting of:
(i) a crystalline homopolymer of propylene having an isotactic index greater than 80;
(ii) a crystalline copolymer of propylene and an olefin selected from the group consisting of ethylene and C4-C10 xcex1-olefins, provided that when the olefin is ethylene, the maximum polymerized ethylene content is 10% by weight, preferably about 4%, and when the olefin is a C4-C10 xcex1-olefin, the maximum polymerized content thereof is 20% by weight, preferably about 16%, the copolymer having an isotactic index greater than 85;
(iii) a crystalline terpolymer of propylene and two olefins selected from the group consisting of ethylene and C4-C8 xcex1-olefins, provided that the maximum polymerized C4-C8 xcex1-olefin content is 20% by weight, preferably about 16%, and, when ethylene is one of the olefins, the maximum polymerized ethylene content is 5% by weight, preferably about 4%, the terpolymer having an isotactic index greater than 85;
(iv) a thermoplastic olefin comprising:
(1) about 10% to about 60%, preferably about 20% to about 50%, of a propylene homopolymer having an isotactic index greater than 80, or a crystalline copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene, and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content greater than 85% and an isotactic index of greater than 85%;
(2) about 20% to about 60%, preferably about 30% to about 50%, of an amorphous copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% of a polymerized diene, and containing less than 70% polymerized ethylene and being soluble in xylene at ambient temperature; and
(3) about 3% to about 40%, preferably about 10% to about 20%, of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature,
wherein the composition has a flexural modulus of greater than 150 but less than 1200 MPa;
(v) a heterophasic polyolefin composition comprising:
(1) about 30% to about 98%, preferably about 60% to about 80%, of a polymeric material selected from the group consisting of a propylene homopolymer having an isotactic index greater than 90, and a crystalline copolymer having an isotactic index greater than 85 of propylene and at least one xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C6 alkyl group, the polymerized xcex1-olefin being less than 10% of the copolymer when R is H and being less than 20% when R is a C2-C6 alkyl group or a combination thereof with R=H, and
(2) about 2% to about 70%, preferably about 20% to about 40%, of an elastomeric copolymer of propylene and an xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C8 alkyl group, the polymerized xcex1-olefin being about 45% to about 75%, preferably about 50% to about 70%, of the elastomeric copolymer, and about 10% to about 40% of the elastomeric copolymer being insoluble in xylene at ambient temperature, or an elastomeric copolymer of ethylene and a C4-C8 xcex1-olefin, having a polymerized xcex1-olefin content of about 15% to about 60%, preferably about 15% to about 40%, and
(vi) a graft copolymer comprising a backbone of a propylene polymer material, having graft polymerized thereto polymerized monomers selected from the group consisting of: (I) at least one acrylic monomer, (II) at least one styrenic monomer, and (III) mixtures of (I) and (II),
wherein (a)+(b)+(c)+(d)=100%, and
wherein layer (1) comprises about 5% to about 60% of the total thickness of the sheet.
The high melt strength propylene polymer (a)(i) in layer (2) is preferably a normally solid, high molecular weight, gel-free, predominantly isotactic, semi-crystalline propylene homopolymer, or a copolymer of propylene and ethylene or a 4-10 C alpha-olefin, provided that when the olefin is ethylene, the maximum polymerized ethylene content is 5%, preferably about 4%, by weight, and when the olefin is a 4-10 C alpha-olefin, the maximum polymerized content thereof is about 20%, preferably about 16%, by weight. The branching index of the propylene homopolymer and copolymer is less than 1, and both have strain hardening elongational viscosity.
The branching index quantifies the degree of long chain branching. In preferred embodiments the branching index of the propylene polymer in (a)(i) of layer (2) is preferably less than about 0.9, and most preferably about 0.3 to 0.5. It is defined by the equation:       g    xe2x80x2    =                              [          IV          ]                Br                              [          IV          ]                Lin                        ❘              M        w
in which gxe2x80x2 is the branching index, [IV]Br is the intrinsic viscosity of the branched propylene polymer material, and [IV]Lin is the intrinsic viscosity of a normally solid, predominantly isotactic, semi-crystalline, linear propylene polymer material of substantially the same weight average molecular weight, and, in the case of copolymers, substantially the same relative molecular proportion of monomer units.
Intrinsic viscosity, also known as the limiting viscosity number, in its most general sense is a measure of the capacity of a polymer molecule to enhance the viscosity of a solution. This depends on both the size and the shape of the dissolved polymer molecule. In comparing a non-linear polymer with a linear polymer of substantially the same weight average molecular weight, the intrinsic viscosity is an indication of the configuration of the non-linear polymer molecule. The above ratio of intrinsic viscosities is a measure of the degree of branching of the non-linear polymer. A method for determining the intrinsic viscosity of propylene polymer materials is described by Elliott et al., J. App. Poly. Sci., 14, 2947-2963 (1970). The intrinsic viscosity is determined with the polymer dissolved in decahydronaphthalene at 135xc2x0 C.
Weight average molecular weight can be measured by various procedures. However, the procedure preferably used here is that of low angle laser light scattering photometry, which is disclosed by McConnell in Am. Lab., May 1978, in the article entitled xe2x80x9cPolymer Molecular Weights and Molecular Weight Distribution by Low-Angle Laser Light Scatteringxe2x80x9d.
Elongational viscosity is the resistance of a fluid or semi-fluid substance to elongation. It is a melt property of a thermoplastic material that can be determined by an instrument that measures the stress and strain of a specimen in the melt state when subjected to tensile strain at a constant rate. One such instrument is described and shown in FIG. 1 of Munstedt, J. Rheology, 23, (4), 421-425 (1979). A commercial instrument of similar design is the Rheometrics RER-9000 extensional rheometer. Molten, high molecular weight, linear propylene polymer material exhibits elongational viscosity which, as it is elongated or drawn at a constant rate from a relatively fixed point, tends to increase for a distance dependent on the rate of elongation, and then to decrease rapidly until it thins to nothing- so-called ductile or necking failure. On the other hand, the molten propylene polymer material of this invention, that is of substantially the same weight average molecular weight and at substantially the same test temperature as the corresponding molten, high molecular weight, linear, propylene polymer material, exhibits elongational viscosity which, as it is elongated or drawn from a relatively fixed point at substantially the same rate of elongation tends to increase over a longer distance, and to break or fail by fracture- so-called brittle or elastic failure. These characteristics are indicative of strain hardening. The more long chain branching the propylene polymer material of this invention has, the greater the tendency of the elongational viscosity to increase as the elongated material approaches failure. This latter tendency is most evident when the branching index is less than about 0.8.
The high melt strength polymers can be made by treating a normally solid, predominantly crystalline propylene polymer without strain hardening elongational viscosity with a low decomposition temperature peroxide or with high energy ionizing radiation in the substantial absence of atmospheric oxygen, for example, in an environment in which an active oxygen concentration of less than about 15% by volume is maintained. The peroxide-treated or irradiated propylene polymer is then heated or treated with a free radical scavenger in the substantial absence of atmospheric oxygen to deactivate substantially all of the free radicals present in the propylene polymer.
The preparation of the high melt strength propylene polymers having strain hardening elongational viscosity is described in more detail in U.S. Pat. Nos. 5,047,446 and 5,047,485, which are incorporated herein by reference.
Alternatively, the high melt strength propylene polymer used in (a)(i) of layer (2) can be characterized by at least (a) either a Mz of at least 1.0xc3x97106 or a Mz/Mw ratio of at least 3.0, and (b) either an equilibrium compliance Jeo of at least 12xc3x9710xe2x88x925 cm2/dyne or a recoverable shear strain per unit stress Sr/S of at least 5xc3x9710xe2x88x925 cm2/dyne at 1 secxe2x88x921.
The molecular weight distribution in a sample of the propylene polymer material can be determined by high temperature gel permeation chromatography (GPC). The Waters 150 CV GPC chromatograph can be used at 135xc2x0 C. with trichlorobenzene as the carrier solvent and a set of Waters xcexc-Styragel HT, 103, 104, 105 and 106 columns. The solution concentration is 0.2% (w/v) and the flow rate is 1 ml/min.
The rheological characterization of the propylene polymer materials can be conducted with a programmed Rheometrics Mechanical Spectrometer (RMS-800). Resin pellets are compression molded into sheets from which samples are stamped out with a 25 mm diameter circular die. Tests are conducted at 210xc2x11xc2x0 C. using 25 m parallel plate geometry with a 1.4mm gap. Creep data are obtained under a constant stress of 1000 dyne/cm2 for a period of 0-300 sec. The creep compliance J(t) is given by
J(t)=xcfx84(t)/"sgr"o=Jeo+t/xcex7o
where
xcfx84=strain
"sgr"o=stress
Jeo=equilibrium compliance
xcex7o=zero shear viscosity
The equilibrium compliance Jeo is a measure of melt elasticity and is determined by first plotting strain against time at constant stress. The strain as a function of time is divided by the stress to give J(t). Jeo is the intercept of the J(t) against time plot.
The recoverable shear strain per unit stress Sr/S also distinguishes the high melt strength propylene polymer materials. This quantity is a fundamental measure of melt elasticity. Using the programmed Rheometrics Mechanical Spectrometer, the polymer melt is subjected to clockwise rotational shear strain by the driver and the resulting shear stress S and first normal stress N1 are measured by a transducer. The shear rate range is 0.01 to 10 sxe2x88x921, the time before measurement is 2.2 min and the time of the measurement is 0.3 min. Normal stress measurements are obtained at each shear rate. The recoverable shear strain Sr is obtained from the first normal stress difference N1.   Sr  =            N      1              2                    xe2x80x83                  S
The normalized quantity Sr/S, i.e., recoverable shear strain per unit stress is a measure of melt elasticity.
The chopped glass fibers that are optionally present in layer (2) have a maximum length of xc2xd inch and can optionally be coated with an aminosilane. The optional glass fibers can be used alone as component (a) in layer (2) or in combination with the propylene polymer material having strain hardening elongational viscosity. When used, the glass fibers are present in an amount of about 5% to about 40%, preferably about 15% to about 25%, based on the total weight of the materials in layer (2).
When glass fibers are present in layer (2), a coupling agent can also be used. The coupling agent can be, for example, polypropylene modified with an xcex1,xcex2-unsaturated carboxylic acid or alicyclic carboxylic acid and derivatives thereof, such as, for example, acrylic acid, methacrylic acid, maleic acid, fumaric acid, itaconic acid, endocyclo(2,2,1)-5-heptene-2,3-carboxylic acid, and cis-4-cyclohexene-1,2-carboxylic acid and anhydrides, esters, amides, and imides thereof. Polypropylenes modified with various amounts of maleic anhydride or maleic acid are preferred and are available commercially, for example, from Eastman Chemical Company and Aristech Chemicals. The modified polypropylenes generally contain about 0.5% to about 10% of maleic acid or maleic anhydride, based on the total weight of the modified polymer. When present, the coupling agent is used in an amount of about 0.5% to about 7%, preferably about 1% to about 5%, based on the total weight of the materials in layer (2).
Optional component (2)(b) is an inorganic filler such as, for example, talc, calcium carbonate, or a silicate. The use of a filler is preferred. Calcium carbonate is the preferred filler. The total amount of chopped glass fibers plus inorganic filler, when present, is not greater than 50%.
The total amount of polymerized ethylene in (2)(c) is preferably about 10% to about 40% by weight.
The C4-8 xcex1-olefins useful in the preparation of (2)(c) and (2)(d)(iv) include, for example, butene-1; pentene-1; hexene-1; 4-methyl-1-pentene, and octene-1.
The diene, when present, is typically a butadiene; 1,4-hexadiene; 1,5-hexadiene, or ethylidenenorbornene.
Room or ambient temperature is xcx9c25xc2x0 C.
Propylene polymer materials (c) and (d)(iv) can be prepared by polymerization in at least two stages, where in the first stage the propylene, or propylene and ethylene or xcex1-olefin, or propylene, ethylene and the xcex1-olefin are polymerized to form component (c)(i) or (d)(iv)(1), and in the following stages the mixtures of ethylene and propylene or the xcex1-olefin, or ethylene, propylene and the xcex1-olefin, and optionally a diene, are polymerized to form components (c)(ii) and (c)(ii) or (d)(iv)(2) and (3).
The polymerization can be conducted in liquid phase, gas phase, or liquid-gas phase using separate reactors, all of which can be done either by batch or continuously. For example, it is possible to carry out the polymerization of component (c)(i) or (d)(iv)(1) using liquid propylene as a diluent, and the polymerization of components (c)(ii) and (iii) and (d)(iv)(2) and (3) in gas phase, without intermediate stages except for the partial degassing of the propylene. An all gas phase process is the preferred method.
The preparation of propylene polymer material (c) is described in more detail in U.S. Pat. Nos. 5,212,246 and 5,409,992, which are incorporated herein by reference. The preparation of propylene polymer material (d)(iv) is described in more detail in U.S. Pat. Nos. 5,302,454 and 5,409,992, which are incorporated herein be reference.
The 2-8 C olefins in (c) include linear and branched alpha-olefins such as, for example, 1-butene; isobutylene; 1-pentene; 1-hexene; 1-octene; 3-methyl-1-butene; 4-methyl-1-pentene; 3,4-dimethyl-1-butene, and 3-methyl-1-hexene.
The heterophasic polyolefin composition (d)(v) can be obtained by sequential polymerization of monomers in the presence of Ziegler-Natta catalyst, or by mechanical blending of components (1) and (2). A suitable sequential polymerization process is described in more detail in U.S. Pat. No. 5,486,419, which is incorporated herein by reference.
The graft copolymer (2)(d)(vi) is the same as the graft copolymer (a)(ii) in layer (1).
Preferably at least one of the propylene polymer materials listed under (d) is present.
Layer (2) is about 40% to about 95% of the total thickness of the laminate.
Additives such as pigments, metallic flake, slip agents, waxes, oils, antiblocking agents, and antioxidants can also be present in the compositions used to form the layers of the co-extruded sheets of this invention.
The process for making the co-extruded sheets of this invention comprises co-extruding a multi-layer sheet comprising:
(1) at least one outer layer comprising (a) a propylene polymer material selected from the group consisting of (i) a propylene homopolymer or a copolymer of propylene and ethylene or a 4-8 C alpha-olefin, both having a melt flow rate of 0.5 to 15 dg/min, wherein the polymerized ethylene or polymerized alpha-olefin content of the copolymer is not greater than 20%, and (ii) a graft copolymer comprising a backbone of a propylene polymer material, having graft polymerized thereto polymerized monomers selected from the group consisting of (I) at least one acrylic monomer, (II) at least one styrenic monomer, and (III) mixtures of (I) and (II), and (b) about 0.15% to about 0.70%, preferably about 0.2% to about 0.4%, of a nucleating agent having a melting point greater than 265xc2x0 C. when the propylene polymer material is (i) or about 0.5% to about 1.5%, preferably about 0.7% to about 1.3%, of a nucleating agent having a melting point greater than 265xc2x0 C. when the propylene polymer material is (ii), and
(2) another layer comprising:
(a) a material selected from the group consisting of (i) about 5% to about 50%, preferably about 15% to about 30%, of a propylene polymer having strain hardening elongational viscosity selected from the group consisting of (I) a propylene homopolymer and (II) a copolymer of propylene and ethylene or a 4-10 C alpha-olefin, provided that when the olefin is ethylene, the maximum polymerized ethylene content is about 5%, and when the olefin is a 4-10 C alpha-olefin, the maximum polymerized content thereof is 20%, (ii) about 5% to about 40%, preferably about 15% to about 25%, of chopped glass fibers having a maximum length of xc2xd inch, and (iii) a mixture of (i) and (ii),
(b) optionally about 5% to about 40%, preferably about 10% to about 30%, of an inorganic filler, the total amount of chopped glass fibers plus inorganic filler, when present, being not greater than 50%,
(c) about 2% to about 50%, preferably about 10% to about 30%, of an olefin polymer composition comprising
(i) about 10 parts to about 60 parts by weight, preferably about 15 to about 55 parts, of a crystalline propylene homopolymer having an isotactic index greater than 80, preferably about 85 to about 98, or a crystalline copolymer from monomers selected from the group consisting of (1) propylene and ethylene, (2) propylene, ethylene and a C4-C8 xcex1-olefin, and (3) propylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content of more than 85% by weight, preferably about 90% to about 99%, and an isotactic index greater than 85;
(ii) about 5 parts to about 25 parts by weight, preferably about 5 parts to about 20 parts, of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature; and
(iii) about 30 parts to about 70 parts by weight, preferably about 20 parts to about 65 parts, of an elastomeric copolymer from monomers selected from the group consisting of (1) ethylene and propylene, (2) ethylene, propylene, and a C4-C8 xcex1-olefin, and (3) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% by weight of a polymerized diene, and containing less than 70% by weight, preferably about 10% to about 60%, most preferably about 12% to about 55%, of polymerized ethylene and being soluble in xylene at ambient temperature and having an intrinsic viscosity measured in decahydronaphthalene at 135xc2x0 C. of about 1.5 to about 4.0 dl/g;
the total of (ii) and (iii), based on the total olefin polymer composition being from about 50% to about 90%, and the weight ratio of (ii)/(iii) being less than 0.4, preferably 0.1 to 0.3, wherein the composition is prepared by polymerization in at least two stages and has a flexural modulus of less than 150 MPa; and
(d) optionally about 5% to about 70%, preferably about 30% to about 60%, of at least one propylene polymer material selected from the group consisting of:
(i) a crystalline homopolymer of propylene having an isotactic index greater than 80;
(ii) a crystalline copolymer of propylene and an olefin selected from the group consisting of ethylene and C4-C10 xcex1-olefins, provided that when the olefin is ethylene, the maximum polymerized ethylene content is 10% by weight, preferably about 4%, and when the olefin is a C4-C10 xcex1-olefin, the maximum polymerized content thereof is 20% by weight, preferably about 16%, the copolymer having an isotactic index greater than 85;
(iii) a crystalline terpolymer of propylene and two olefins selected from the group consisting of ethylene and C4-C8 xcex1-olefins, provided that the maximum polymerized C4-C8 xcex1-olefin content is 20% by weight, preferably about 16%, and, when ethylene is one of the olefins, the maximum polymerized ethylene content is 5% by weight, preferably about 4%, the terpolymer having an isotactic index greater than 85;
(iv) a thermoplastic olefin comprising:
(1) about 10% to about 60%, preferably about 20% to about 50%, of a propylene homopolymer having an isotactic index greater than 80, or a crystalline copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene, and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer having a polymerized propylene content greater than 85% and an isotactic index of greater than 85%;
(2) about 20% to about 60%, preferably about 30% to about 50%, of an amorphous copolymer from monomers selected from the group consisting of (a) ethylene and propylene, (b) ethylene, propylene and a C4-C8 xcex1-olefin, and (c) ethylene and a C4-C8 xcex1-olefin, the copolymer optionally containing about 0.5% to about 10% of a polymerized diene, and containing less than 70% polymerized ethylene and being soluble in xylene at ambient temperature; and
(3) about 3% to about 40%, preferably about 10% to about 20%, of a copolymer of ethylene and propylene or a C4-C8 xcex1-olefin that is insoluble in xylene at ambient temperature,
wherein the composition has a flexural modulus of greater than 150 but less than 1200 MPa;
(v) a heterophasic polyolefin composition comprising:
(1) about 30% to about 98%, preferably about 60% to about 80%, of a polymeric material selected from the group consisting of a propylene homopolymer having an isotactic index greater than 90, and a crystalline copolymer having an isotactic index greater than 85 of propylene and at least one xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C6 alkyl group, the polymerized xcex1-olefin being less than 10% of the copolymer when R is H and being less than 20% when R is a C2-C6 alkyl group or a combination thereof with R=H, and
(2) about 2% to about 70%, preferably about 20% to about 40%, of an elastomeric copolymer of propylene and an xcex1-olefin of the formula CH2xe2x95x90CHR, where R is H or a C2-C8 alkyl group, the polymerized xcex1-olefin being about 45% to about 75%, preferably about 50% to about 70%, of the elastomeric copolymer, and about 10% to about 40% of the elastomeric copolymer being insoluble in xylene at ambient temperature, or an elastomeric copolymer of ethylene and a C4-C8 xcex1-olefin, having a polymerized xcex1-olefin content of about 15% to about 60%, preferably about 15% to about 40%, and
(vi) a graft copolymer comprising a backbone of a propylene polymer material, having graft polymerized thereto polymerized monomers selected from the group consisting of: (I) at least one acrylic monomer (II) at least one styrenic monomer, and (III) mixtures of (I) and (III),
wherein (a)+(b)+(c)+(d)=100% and,
wherein layer (1) comprises about 5% to about 60% of the total thickness of the sheet,
at a polymer melt temperature of 230xc2x0-255xc2x0 C., preferably about 238xc2x0-250xc2x0 C., as it comes from the extruder die.
The combination of extruding at a temperature above the melting point of polypropylene and the use of a nucleating agent having a melting point above 265xc2x0 C. is required to obtain high surface gloss after melt phase thermoforming.
In addition to a co-extruded sheet comprising the two layers just described, sheets with additional layers on the back of layer (2) can also be made, e.g., another layer having the same composition as layer (1) or a layer made from reground polymer scrap from the manufacture of the co-extruded sheet. When glass fibers are present in layer (2), there is always a third layer present on the back of layer (2).
The co-extruded sheets are typically 100-300 mils thick, although sheets with thicknesses above and below this range can also be made, and are within the broadest ambit of this invention.
The co-extruded sheets of this invention exhibit a combination of (1) good gloss, (2) hardness, (3) good plate impact, (4) good melt phase thermoformability, and (5xc2x0)no delamination of layers on impact. In addition, when glass fibers are present in layer (2), the co-extruded sheets have significantly increased flexural modulus, i.e., a minimum increase of 50% compared with a similar polymer matrix without glass reinforcement, while maintaining good impact strength. Typically impact strength decreases when the flexural modulus of a material is increased.
The co-extruded sheets can be used for applications such as co-extruded profiles; boat hulls and boat decks as well as boat engine covers, consoles, hatches, and other boat parts; indoor and outdoor whirlpool tubs or hot tubs; swimming pools; camper tops; household appliance cabinets and door liners; pick-up truck caps; structural and body components for golf carts; sinks; tractor hoods; automobile body panels; outdoor portable toilets; shower stalls; wall panels; counter tops; electrical equipment housings; body panels and engine shrouds for all-terrain vehicles, tractors, and combines; engine covers and body panels for jet skis and snowmobiles, and replacement exterior auto body panels.
A molded part can be made by thermoforming the co-extruded sheets of this invention. The thermoforming process is well known to those skilled in the art and is described, for example, in D. V. Rosato, Rosato""s Plastics Encyclopedia and Dictionary, Hanser Publishers, 755-757 (1993). The process usually consists of heating a thermoplastic sheet, film, or profile to its softening temperature and forcing the hot and flexible material against the contours of a mold by pneumatic means (differentials in air pressure are created by pulling a vacuum between the plastic and the mold, or the pressure of compressed air is used to force the material against the mold), mechanical means (plug or matched mold, for example), or combinations of pneumatic and mechanical means. The process involves (1) heating the sheet in a separate oven and then transferring the hot sheet to a forming press, (2) using automatic machinery to combine heating and forming in a single unit, or (3) a continuous operation feeding off a roll of thermoplastic material or directly from the exit of an extruder die (post-forming).
In the melt phase process for thermoforming the co-extruded sheets of this invention, the surface temperature of the nucleated propylene polymer material layer (1) is at least 310xc2x0 F. When the propylene polymer material is a propylene homopolymer or copolymer, the surface temperature is typically is about 310xc2x0 to about 370xc2x0 F. When the propylene polymer material is a graft copolymer, the surface temperature is typically about 370xc2x0 to about 410xc2x0 F.
The co-extruded sheets have a surface gloss of greater than 80 measured at a reflected light angle of 60xc2x0. Thermoformed parts made from the co-extruded sheets can have a surface gloss as high as 87.
Another embodiment of this invention is a composite material comprising (a) at least one layer of the sheet or the thermoformed article of this invention and (b) a layer of a low density polyolefin foam having a density of about 1 to about 15 lb/f3 and a thickness of about xe2x85x9 inch to about 4 inches, preferably  greater than 1 inch up to 3 inches. The low density foam layer can be an extruded foam sheet or plank, or the layer can be molded from foam beads. The low density foam layer can comprise a single thickness of foam, or several thin layers attached to each other, e.g., thermally, such as by the use of a xe2x80x9chot knifexe2x80x9d, or by the use of a suitable adhesive such as, for example, low molecular weight polyolefins made from functionalized unsaturated monomers with polar groups such as monounsaturated carboxylic acids or their anhydride derivatives such as maleic or itaconic acid or their anhydrides, or unfunctionalized unsaturated monomers; hot melt adhesives, or aqueous- or solvent-based emulsions. Suitable bonding agents include, for example, hydrogenated hydrocarbon resins such as Regalrez tackifiers, commercially available from Hercules Incorporated, and Arkon P tackifiers, commercially available from Arakawa Chemical (U.S.A.) Incorporated; 1023PL amorphous polypropylene tackifying agent available from Eastman Chemical Company, and predominantly amorphous ethylene/propylene copolymers commonly known as ethylene/propylene rubber (EPR).
The foam and the co-extruded sheet can be thermoformed separately and then joined, for example, either thermally or by the use of a suitable adhesive such as those described in the preceding paragraph, or they can be laminated during the forming process.
The polyolefin used to make the foam is preferably the same as the high melt strength propylene polymer having strain hardening elongational viscosity described in (2)(a)
Extruded foam sheets can be made by conventional techniques such as, for example, using a tandem extrusion line. The process consists of mixing the propylene polymer having a high melt strength and high melt elasticity with a nucleating agent in a primary extruder, kneading the mixture, injecting a physical blowing agent into the mixture to form a foaming mixture, transferring the foaming mixture to a secondary extruder, mixing and cooling the foaming mixture, and extruding the foaming mixture through an annular or flat die into a continuous foam sheet. Suitable nucleating agents include a mixture of citric acid and sodium bicarbonate, talc, and titanium dioxide. Suitable blowing agents include hydrocarbons such as butane and isopentane, chlorinated hydrocarbons, chlorofluorocarbons, nitrogen, carbon dioxide, and other inert gases.
Low density foam layers molded from foam beads can be made, for example, by making prefoamed beads by extruding a high melt strength propylene polymer in the presence of a foaming agent such as, for example, pentane, hexane, dichlorotrifluoroethane and methylene chloride. One or more nucleating agents such as talc, colloidal silica, sodium bicarbonate or its blends with citric acid, and azodicarbonamide, can be added to the polymer before or during extrusion. The prefoamed beads are then thermoformed by sintering. A mold having the desired dimensions is filled with the prefoamed beads and the beads are heated by passing a hot pressurized gas such as superheated steam through the mold to obtain sintering and produce the finished article. Such a process is described, for example, in U.S. Pat. No. 5,324,753, which is incorporated herein by reference.
The composite materials can be used for making large structural parts, for example by pressure or melt thermoforming techniques. Examples of parts that can be made from these materials include co-extruded profiles; household appliance cabinets and door liners; hot tubs; and boat hulls and boat decks as well as boat engine covers, consoles, and hatches. The particular combination of materials used is determined by the properties desired in the thermoformed part.
The test methods used to evaluate the properties of the co-extruded sheets were:
All gloss readings were taken with a 60 degree gloss meter from a smooth (ungrained) sample.
Isotactic index is defined as the percent of olefin polymer insoluble in xylene. The weight percent of olefin polymer soluble in xylene at room temperature is determined by dissolving 2.5 g of the polymer in 250 ml of xylene at room temperature in a vessel equipped with a stirrer, and heating at 135xc2x0 C. with agitation for 20 minutes. The solution is cooled to 25xc2x0 C. while continuing the agitation, and then left to stand without agitation for 30 minutes so that the solids can settle. The solids are filtered with filter paper, the remaining solution is evaporated by treating it with a nitrogen stream, and the solid residue is vacuum dried at 80xc2x0 C. until a constant weight is reached. The percent by weight of polymer insoluble in xylene at room temperature is the isotactic index of the polymer. The value obtained in this manner corresponds substantially to the isotactic index determined via extraction with boiling n-heptane, which by definition constitutes the isotactic index of the polymer.
Intrinsic viscosity is measured in decahydronaphthalene at 135xc2x0 C.
For the sag resistance test a thermoforming oven is heated to 450xc2x0 F. A sheet measuring xcx9c8.5xe2x80x3 wide and xcx9c18xe2x80x3 long is clamped at two ends in a frame. The frame is on rollers and the clamped sheet is rolled into the oven. The sheet is kept in the oven until it sags a distance of 3xe2x80x3. The time it takes to sag 3xe2x80x3 is recorded and reported as sag resistance.
In this specification, all parts and percentages are by weight unless otherwise noted.

High surface gloss, co-extruded sheets from olefin polymer materials


In a geared motor for a self-traveling carrier, a projected area in an advancing direction of the carrier is made small to reduce the space required around a track. Despite the fact that the geared motor being is a single type of a geared motor (the same geared motor), it is possible to select a suitable mounting mode from among various mounting modes, thus permitting a smoother operation of a physical distribution system as a whole. For example, in a geared motor for a self-traveling carrier, a reduction mechanism housed in a gear box incorporates an output shaft with a wheel mounted thereon, an output shaft gear, an intermediate shaft disposed in parallel with the output shaft, an intermediate pinion and a hypoid gear both mounted on the intermediate shaft, and a hypoid pinion mounted on a motor shaft. The motor shaft is disposed between the intermediate shaft and the output shaft orthogonally thereto. Further, three faces of the gear box are used as mounting faces for mounting the geared motor to the carrier.

1. Field of the Invention
The present invention relates to a geared motor for a self-traveling carrier wherein a motor for driving a wheel of the self-traveling carrier adapted to travel through the rolling of the wheel on a track, and a gear box housing therein a speed change mechanism disposed between a motor shaft of the motor and the wheel, are rendered integral with each other.
2. Description of the Prior Art
In Japanese Utility Model Laid Open No. 55166/89 there is disclosed a self-traveling carrier of a conveyor for use in a physical distribution system. This self-traveling carrier, as shown in FIG. 7, is provided with a driving trolley 11 and a driven trolley 12 both capable of moving along a traveling rail (track) 2 and disposed of intervals from each other in the longitudinal direction, a connecting member 13 for connecting both trolleys 11 and 12, and a goods table 15 mounted to the connecting member 13 through a pair of front and rear hangers 14.
As shown in FIG. 8, the driving trolley 11 is provided with a driving roller (wheel) 16 adapted to roll on an upper surface of an upper flange of the traveling rail 2, four guide rollers 17 disposed on both sides of the upper flange of the rail 2 and of a lower flange of the rail, an electric motor 18 for rotating the driving roller 16, a reduction mechanism 19 with a clutch device disposed between the driving roller 16 and the electric motor 18, and a gear box 50 which houses therein the reduction mechanism 19 with a clutch device.
According to the construction of the reduction mechanism 19, power is transmitted to an output shaft 23 through a pinion 30 mounted on a motor shaft 29, a gear 34 meshing with the pinion 30, a bevel pinion 35 formed integrally with an intermediate shaft 33 onto which is fixed the gear 34, and further through a bevel gear 28 meshing with the bevel pinion 35.
Though not shown, there is also provided a current collector adapted to slide on a current collector rail 3.
Upon rotation of the motor 18, the driving roller 16 rotates through the reduction mechanism 19 with a clutch device, so that the driving trolley 11 travels on the traveling rail 12. Consequently, the driven trolley 12 connected to the driving trolley through the connecting member 13 also travels on the rail 2, whereby the goods table 15 mounted to the connecting member 13 through the hangers 14 can be moved.
Further, even in the event of occurrence of trouble or the like, the self-traveling carrier can be easily moved manually because the mechanical connection between the motor shaft 29 and the driving roller 16 can be released by the function of the clutch device.
In such a conventional self-traveling carrier, however, there have been the following problems associated with its geared motor portion (the portion including both the motor and the gear box).
a: Since there is adopted a structure wherein the motor 18 is suspended vertically on the side of output shaft 23 projecting in the direction opposite to the driving roller 16 with respect to a bearing portion (indicated at numerals 21 and 22 in FIG. 8) which bears the wheel load, a projected area of the geared motor in the advancing direction of the carrier 1 corresponds to an "axial sectional area" of the geared motor and thus it is very large.
More particularly, from the nature of the carrier which travels on the track, it is necessary that an "obstacle-free space" larger than the projected area in the advancing direction of the carrier is ensured around the track and throughout the whole section of the track. Therefore, if the projected area in the carrier advancing direction of the geared motor is large, the mounting of the self-traveling carrier itself may be impossible, or it will be impossible to utilize the space around the track effectively for other purposes.
b: The reduction mechanism portion comprises such conventional combinations as the pinion 30--gear 34 and the bevel pinion 35--bevel gear 28, also, the projection of the clutch device portion is fairly large, so the reduction in size of the gear box into a compact size is not attained, and the projected area itself of the gear box is also large.
c: The mounting of the geared motor to the carrier is exclusively for the self-traveling carrier, so with one type of a gear box, it is impossible to cope with various mounting methods.
This point will now be explained more concretely. In a physical distribution system or the like comprising a plurality of self-traveling carriers for example, it is efficient to operate of the system a necessary portion only when required. In driving the self-traveling carriers, it is more convenient for each self-traveling carrier to be independent. Also, it is often necessary to change the position of each self-traveling carrier for changing a conveyance path. Also, in such cases, it is more convenient for each self-traveling carrier to be independent.
For this reason, as in the above conventional example, a self-traveling carrier with a "motor," more exactly a self-traveling carrier with a "geared motor" comprising a motor and a speed change mechanism (generally a reduction mechanism), has become popular. Therefore, in this case, when viewed from the entire self-traveling carrier, the "geared motor" merely constitutes a portion of the carrier. Also as to each self-traveling carrier, it merely constitutes a portion of the physical distribution system when viewed from the whole of the system.
In relation to the entire physical distribution system, therefore, various members which are obstacles to the mounting of the geared motor are often present around the self-traveling carriers. Further, with respect to a self-traveling carrier which is already in use, in the case where a certain member is newly present within a projected area in the advancing direction of that carrier, it sometimes becomes impossible for the geared motor portion of the carrier to remain mounted as it is.
In such a case, the foregoing prior art permits only "one face" to effect mounting of the geared motor portion of the self-traveling carrier and hence it is impossible to effect various modes of mounting correspondingly to the positions of other devices and members.
Generally, in such a case, it is necessary to beforehand provide various geared motors different in the mounting face and mounting method and to select a suitable geared motor according to conditions. As the entire physical distribution system, however, it is not desirable to provide a variety of geared motors, from the standpoint of maintenance and control of the system.

Geared motor for self-travelling carrier


A flanging-trimming machine for differently shaped panels having peripheral edges. The machine covers the edges with an irremovable covering strip applied using an adhesive. The machine includes (a) a main supporting structure, (b) a reservoir having the adhesive therein, (c) a means for supporting, transporting, and positioning said panels which is displaceable with a rectilinear reciprocating movement along a first horizontal and longitudinal axis X and a second horizontal and traversal axis Y which is orthogonal to the axis X and which is displaceable with a rotational reciprocating movement along a third axis W which is orthogonal to the axes X and Y, (d) a preassembled spool of the material for the strips, (e) a means for applying the strips to the edges which is associated with a means to dispense the strips and which is adapted to apply the adhesive to the edges and thereafter to apply the strips to the edges, (f) a cutting means for cutting the strips to the proper size, (g) a trimming means for trimming along the strips after application, and (h) a scraping means for finishing the surface of the strips after application.

Flanging machines of the kind referred to are known for applying irremovably covering strips against the corresponding peripheral edges of differently shaped panels made of wood, chip wood, plastic and similar materials, into which the panels to be coated along the edges are arranged, which panels are prepared and cut in advance with the pre-established shapes and sizes by means of machining steps performed with operative machines of conventional type, and such panels are progressively coated along their peripheral edges by corresponding covering strips made of wood, plastic or other suitable materials, in such a way that they are fixed against such edges without the possibility to disjoin therefrom.
In order to perform this, these covering strips are coated in advance with suitable adhesive materials such as for instance thermomeltable glues of conventional type onto the surface thereof to be fixed against said peripheral edges, which operation is normally performed in a particular operative station of the machine and consists in drawing by a roll the adhesive material contained into a proper reservoir and transferring such adhesive material onto the surface of the strips to be applied against the different peripheral edges of each panel, by means of contact of such roll against the surface referred to, and afterwards the strips so coated with adhesive material are pressed by an additional machine pressing roll against the peripheral edges of each panel, thereby providing a close irremovable junction therewith.
Such covering strips may be also pre-coated with adhesive materials on other areas of the processing factory, so that these strips so arranged in the flanging machines referred to are firstly heated at temperatures enough to soften the same adhesive materials, and thereafter fixed as described above against the peripheral edges of each panel.
However, the flanging machines of the kind described have evident applicative limits, ascribable above-all to the fact that they are able to perform satisfactory flanging operations of panels with rectilinear outlines only and not with curvilinear and mixed rectilinear-curvilinear outlines, as it would be desirable, since such machines are designed to machine only along Cartesian axes X and Y, which are rectilinear and orthogonal to each other, and therefore cannot perform machinings along bent lines, so that in presence of such profiled panels the flangings thereof cannot be performed automatically with such machines, and must be performed exclusively manually, with consequent drawbacks from the points of view of a lower flexibility and highest burdens in the manufacture of these kinds of panels.


A method is provided to prepare a cationic transition metal catalyst, the method including the steps of: providing a disubstituted phosphine selected from the group consisting of RPH and R.sub.1 R.sub.2 PH wherein R is a divalent group selected from substituted and nonsubstituted hydrocarbon groups, R.sub.1 and R.sub.2 are independently selected from substituted and nonsubstituted hydrocarbon groups; combining the disubstituted phosphine with a salt of the formula R.sub.3 X.sub.n wherein X is a good leaving group and is a weakly coordinating anion and R.sub.3 is a substituted or nonsubstituted aliphatic hydrocarbon and n is 1, 2, or 3 to form a phosphonium salt of a formula selected from R.sub.3 (RP.sup.+ H).sub.n nX.sup.- and R.sub.3 (R.sub.1 R.sub.2 P.sup.+ H).sub.n nX.sup.- ; and combining the phosphonium salt with a transition metal salt of the formula MY.sub.m wherein M is a transition metal, and Y is the anion of a weak acid thereby forming a cationic transition metal catalyst.

Numerous useful processes are catalyzed by transition metal cationic complexes derived from a combination of a transition metal salt, a phosphine ligand, and a strong acid having a weakly or non-coordinating anion. Examples of such processes include hydroformylation of internal olefins, hydroformylation of .alpha.-olefins, acrylic acid produced from acetylene, copolymerization of olefins and carbon monoxide, and production of methyl propionate from ethylene. These cationic phosphine catalysts are typically stable in air, but phosphine precursors to these catalysts can be sensitive to exposure to air. Further, these catalysts have been prepared by multistep synthesis.
For example, U.S. Pat. No. 4,691,047 discloses a process for carbonylation of conjugated dienes with carbon monoxide and an alcohol or water in the presence of an aprotic solvent and a catalytic system prepared by combining a divalent palladium compound, a triarylphosphine and hydrochloric acid. U.S. Pat. No. 5,304,674 discloses an improvement to this process by adding a second diphosphine ligand having electron-releasing substituents on the phosphorus atoms.
European patent application 121,965 A2, 1984, discloses a process for copolymerization of ethylene with carbon monoxide in the presence of methanol using a catalytic system prepared by combining palladium acetate, a diphosphine and p-toluenesulfonic acid.
U. K. patent application 2,101,601A suggests a method to produce bisphosphines by preparation of the bisphosphonium salt followed by hydrolysis of the salt to yield the bisphosphine oxide and then reduction of the bisphosphine oxide to yield a bisphoshine. This method requires an additional process step; a relatively expensive reduction step.
It is therefore an object of the present invention to provide a process to produce a phosphonium salt that can be useful as a component of a catalyst system for reactions between carbon monoxides and olefinic hydrocarbons wherein reactants are not sensitive to exposure to oxygen, and wherein the number of process steps in the process is reduced.

Preparation of transition metal catalysts from phosphonium salts


An electrical heating device employing positive temperature coefficient (PTC) thermistors as heating elements, which provides direct contact between the thermistor heating elements and the radiation units on both sides with no intervening members and which also provides the electrical current to the heating elements via the radiation units.

Positive temperature coefficient (PTC) heating elements, such as thermistors, are used in electrical heating devices, such as electrical radiators, electrical heating fans, and air conditioner heaters. They have an advantage over electric wire heaters in that they are self-regulating as to temperature and thus are not subject to overheating even in response to abnormal electric currents. In many prior art applications employing PTC thermistor heating elements, heat is extracted from the device by air flow through the device, including the heating elements and radiating elements, such as radiating fins. The direct exposure of the PTC elements to the air flow fed to the heating device, however, also exposes these elements to dust, which causes deterioration of their heating ability and efficiency. A further disadvantage of direct exposure of the PTC elements to air flow is the temperature variation between the leeward and windward sides, which reduces heating efficiency and generating power due to the "pinch effect" (current displacement).
U.S. Pat. No. 4,954,692 discloses a heating device employing PTC thermistor heating elements placed in a locating frame made of electric insulating material and located between two radiators provided with flanges which enclose the heating elements, thereby protecting them from direct exposure to air flow. The PTC thermistor heating elements are separated from at least one of the radiators by a plate that is both electrically insulating and heat conducting. Electrical contact with the PTC thermistor is provided by a metallic plate installed between the heating elements and an electric insulating plate. Among the disadvantages of the device disclosed is the requirement of two additional plates between the heating elements and one of the radiators, thereby reducing the efficiency of heat transfer from the heating elements to the radiators and making the device more complicated and more expensive. The requirement of a plate that is both electrically insulating and heat conducting is a further complication and expense.