CA1064738A - Aluminum-iron-nickel alloy electrical conductor - Google Patents
Aluminum-iron-nickel alloy electrical conductorInfo
- Publication number
- CA1064738A CA1064738A CA266,950A CA266950A CA1064738A CA 1064738 A CA1064738 A CA 1064738A CA 266950 A CA266950 A CA 266950A CA 1064738 A CA1064738 A CA 1064738A
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- Prior art keywords
- alloy
- aluminum
- wire
- iron
- nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
- H01B1/023—Alloys based on aluminium
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- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Conductive Materials (AREA)
- Metal Rolling (AREA)
- Continuous Casting (AREA)
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Internal Circuitry In Semiconductor Integrated Circuit Devices (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
This disclosure relates to an aluminum alloy electrical conductor which contains from about 0.20% to about 1.60% by weight nickel, from about 0.30% to about 1.30% iron, optionally up to 2.00% of additional specified alloying elements, and the remainder aluminum with associ-ated trace elements. The conductors are processed in a continuous operation which includes continuous casting, hot-rolling in the as-cast condition to form continuous rod, cold-working of the rod by drawing it through a series of wire-drawing dies, without preliminary or intermediate anneals, and thereafter annealing the wire to achieve a minimum electrical conductivity of 58% IACS, an ultimate tensile strenght of at least 12,000 psi, a yield strength of at least 8,000 psi and an elongation of at least 12%
when measured as a No. 10 A.W.G. wire. The additional alloying elements are precisely controlled in order to facilitate the continuous processing of the cast bar without spitting and cracking of the subsequently rolled and cold-drawn rod.
This disclosure relates to an aluminum alloy electrical conductor which contains from about 0.20% to about 1.60% by weight nickel, from about 0.30% to about 1.30% iron, optionally up to 2.00% of additional specified alloying elements, and the remainder aluminum with associ-ated trace elements. The conductors are processed in a continuous operation which includes continuous casting, hot-rolling in the as-cast condition to form continuous rod, cold-working of the rod by drawing it through a series of wire-drawing dies, without preliminary or intermediate anneals, and thereafter annealing the wire to achieve a minimum electrical conductivity of 58% IACS, an ultimate tensile strenght of at least 12,000 psi, a yield strength of at least 8,000 psi and an elongation of at least 12%
when measured as a No. 10 A.W.G. wire. The additional alloying elements are precisely controlled in order to facilitate the continuous processing of the cast bar without spitting and cracking of the subsequently rolled and cold-drawn rod.
Description
~4'73~
BACKGROUND OF THE_lNVENTION
The present invention relates to an improved aluminum alloy electrical conductor, and the continuous method of production thereof in the form of a rod or wire.
Aluminum base alloys are f inding wider acceptance in the marketplace of today because of their light weight and low cost. One area where aluminum alloys have found increasing acceptance is in the replacement of copper in the manufacture of electrically con,ductive wire.
Conventional electrically conductive aluminum alloy wire (referred to as EC) contains a substantial amount of pure aluminum and trace amounts of impurities such as silicon, vanadium, iron, copper, manganese, magnesium, zinc, boron, and titanium.
Even though desirabla in terms of weight and cost, aluminum alloys have received far less than complete acceptance in the electrical conductor marketplace. One of the chief reasons for the lack of complete acceptance is the range of physical properties available with con-ventional EC aluminum alloy conductors. If the physical properties, such as thermal stability, tensile strength, percent elongation, ductility and yield strength, could be improved significantly without substantially lessening the electrical conductivity of the finished product, a very desirable improvement would be achieved. It is accepted, however, that addition of alloying elements, as in other aluminum alloys, reduces conductivity while improving the phy~ical properties. Consequently, only these additions
BACKGROUND OF THE_lNVENTION
The present invention relates to an improved aluminum alloy electrical conductor, and the continuous method of production thereof in the form of a rod or wire.
Aluminum base alloys are f inding wider acceptance in the marketplace of today because of their light weight and low cost. One area where aluminum alloys have found increasing acceptance is in the replacement of copper in the manufacture of electrically con,ductive wire.
Conventional electrically conductive aluminum alloy wire (referred to as EC) contains a substantial amount of pure aluminum and trace amounts of impurities such as silicon, vanadium, iron, copper, manganese, magnesium, zinc, boron, and titanium.
Even though desirabla in terms of weight and cost, aluminum alloys have received far less than complete acceptance in the electrical conductor marketplace. One of the chief reasons for the lack of complete acceptance is the range of physical properties available with con-ventional EC aluminum alloy conductors. If the physical properties, such as thermal stability, tensile strength, percent elongation, ductility and yield strength, could be improved significantly without substantially lessening the electrical conductivity of the finished product, a very desirable improvement would be achieved. It is accepted, however, that addition of alloying elements, as in other aluminum alloys, reduces conductivity while improving the phy~ical properties. Consequently, only these additions
- 2 - ' ~ID6~ 3~
of elements which improve phy~ical properties without substantially lessening conductivity will yield an acceptable and useful product.
In applicant's prior Canadian Patent ApplicationSerial No. 143~514, Filed May 31J 1972, there is disclosed a new aluminum alloy electrical con-ductor which was formulated to yield improved physical properties with acceptable electrical conductivity. The aluminum base alloy was prepared by mixing nickel, iron and optionally other alloying elements with aluminum in a furnace to obtain a melt having requisite percen*ages of elements. It was found that suitable results were obtained with nickel present in a weight percentage of from about 0.20 percent to about 1.60 percent. Superior results were achieved when nickel was present in a weight percentage of from about 0.50 percent to about 1.00 percent and particularly superior and preferred results were obtained when nickel was present in a percentage by weight of from about 0.60 percent to about 0.80 percent.
Suitable results were obtained with iron present in a weight percentage of from about 0.30 percent to about 1.30 percent. Superior results were achieved when iron was present in a weight percentage of from about 0.40 percent to about 0.80 percent and particularly superior and preferred results were obtained when iron was present in a percentage by weight of from about 0.45 percent to about 0.65 percent.
The aluminum content of the alloy of the afore mentioned patent document could vary from about 97.00 per-cent to about 99.50 percent by weight with superior resultsbeing obtained with the aluminum content between about 97.~0% and about 99.20% by weight. Since the percentage for maximum and minimum aluminum did not correspond with the maximums and minimums for alloying elements, it was apparent that suitable results were not obtained if the ma~imum percentages for all alloying elements were employed. If commercial aluminum was employed in preparing the melt, it was preferred that the aluminum prior to adding to the melt in the furnace, contain no more than 0.10 percent total of trace impurities.
Optionally the alloy of the aforementioned patent document could contain an additional alloying element or group of alloying elements. The total concentration of the optional alloying elements could be up to about 2.00 percent by weight; preferably from about 1.10 percent to about 1.50 percent by weight. Particularly superior and preferred results were obtained when from about 0.10 percent to about 1.00 percent by weight of total additional alloying elements was employed; particularly if at least one element is selected from the sub group of magnesium, niobium, tantalum, silicon and zirconium.
Additional alloying elements included the following:
ADDITIONAL ALLOYING ELEMENTS
.
Magnesium Cesium Dysprosium Cobalt ~ttrium Terbium Copper Scandium Erbium Silicon Thorium Neodynium Zirconium Tin Indium Cerium Zinc Boron a~
Niobium Bismuth Thallium Hafnium Antimony Rubidium Lanthanum Vanadium ~itanium Tantalum Rhenium Carkon Other elements could be present in trace amounts provided that they did not adversely affect the mechanical, electrical and physical properties of the product.
Superior results were obtained with the following additional elements:
PREFERRED ADDITIONAL ALLOY:l:NG ELEMENTS
Magnesium Zirconium Scandium Cobalt Niobium Thorium Copper Tantalum Rare Earth Metals Silicon Yttrium Carbon Particularly superior and preferred results were obtained with the use of cobalt or magnesium as the additional alloying element. Suitable results were obtained with magnesium or cobalt in a percentage range of from about 0.001% to about 1.00~ by weight with superior results being obtained when from about 0.025% to about 0.50~ by weight was used. Particularly superior and preferred results were obtained when from about 0.03% ko about 0.10% by weight of magnesium or cobalt was employed.
While the method of the aforementioned patent specification yielded an aluminum alloy electrical conductor product having improved physical properties as compared with conventional EC aluminum alloy conductors, while main-~6~'73~3 taining comparable electrical conductivityj it did nothave sufficient ductility to facilitate the continuous processing steps, nor to yield a finished wire product having satisfactory elongation characteristics. In par-ticular, the cast bar would tend to split and crack durinc the continuous rolling and cold-drawing thereof, and the wire product often contained intermetallic compound pre-cipitates which, subsequent to cold-drawing of the product, exhibited an insufficient ductility.
STATEMENT OF THE INVENTION
In view of the foregoing, it should be apparent that a need still exists in the art for a method of preparing an aluminum alloy conductor that will improve the ductility of the product manufactured by the process of the aforementioned patent specification, so that such product can be continuously rolled and cold-drawn without splitting and cracking,and so that the wire product will have an elongation of at least 12~ when measured as a No. 10 A.W.G. wire in the fully annealed condition.
In order to accomplish the foregoing, it has been determined in accordance with this invention that the additional alloying elements specified in the aforementioned patent specification must be very closely controlled, with-in predetermined limits, specifically the copper, magnesium and silicon. Thus, there is provided in accordance with this invention a method of preparing an aluminum alloy conductor having a minimum conductivity of at least 58 percent IACS, good thermal stability, a tensile strength of 73~
at least 12,000 psi, and a yield strength of at least 8,000 psi when measured as a fully annealed wire, comprising:
(a) Alloying from 0.20 to 1.60 weight percent nickel, from 0.30 to 1.30 weight percent iron, up to a total of 2.00 wPight percent of additional alloying elements including copper, magnesium and silicon, and from about 97.00 to about 99.50 weigbt percent aluminum with associated trace elements;
(b) Casting the alloy in a moving mold formed between a groove in the periphery of a rotating casting wheel and a metal belt lying adjacent said groove for a portion of its length;
(c) Hot rolling the cast alloy substan-tially immediately after casting while the cast alloy is in substantially that condition as cast to form a continuous rod; and (d~ Drawing the rod through wire-drawing dies, without any preliminary or intermediate anneals between dies, to form wire of finish gauge size;
characterized in that in order to improve the ductility of the product the copper content of the alloy is maintained at less than 0.~5 weight percent, thereby inhibiting the formation of cuprous oxide particles and thus permitting continuous rolling and drawing without splitting and cracking of the product.
The present invention is further characterized in that in order to further improve the ductility of the product the magnesium content of the alloy i5 maintained ~ :lt6~3~3 at les than 0.1 weight percent whan the silicon exceeds 0.15 weight percent, thereby yi~lding a wire having an elongation of at least 12 percent when measured as a No. lO A.W.G. wire in the fully annealed condition.
As expressed above, it has heen determined in accordance with this invention that the copper content must be very closely controlled, within the range specified above, in order to permit continuous processing of the product. Although copper is an effective hardening element, if more than 0.05% copper is present in the alloy of this invention, it will form extremely hard cuprous oxide par-ticles that will result in splitting and cracking when the continuously processed product is rolled and cold drawn.
Since a conventionally processed product can be homogenized prior to rolling to refine the grain structure, the copper content thereof need not be so closely controlled. However, when the product is continuously processed in accordance with the instant invention, the cast bar is substantially immediately rolled in the as-cast condition and thus does not have the benefit of an homogenizing step. Consequently, the copper content o~ the alloy must be closely controlled to avoid the brittleness which leads to splitting and crack-ing of the bar when processed according to the method of this invention.
Similarly, as expressed above, it has been determined in accordance with this invention that the sili-con and magnesium contents must also be very closely controlled. In particular, when the silicon exceeds 0.15 percent, the magnesium must be limited to less than 0.1 ~36~73~
percent; ot~erwise, the product w~ll exhibit an insufficient ductility subsequent to cold drawing, if the product was previously con~inuously cast and rolled.
After preparing the melt in the manner des-cribed in the aforementioned patent specification, with the copper, magnesium and silicon controlled in accordance with the present invention, the aluminum alloy is continuously cast into a continuous bar by a continuous casting machine and then substantially immediately thereafter, hot-worked in a rolling mill to yield a continuous aluminum alloy rod.
An example of a continuous casting and rolling operation capable of producing continuous rod as specified in this application is disclosed in the aforementioned patent speci-fication.
To produce wire of various gau~es, the continuous rod produced by the casting and rolling operation is processed in a reduction operation. The unannealed rod (i.e., as rolled to f temper) is cold-drawn through a series of progressively constricted dies, without preliminary or intermediate anneals, to ~orm a continuous wire of desired diameter. It has been found that the elimination of intermediate anneals improves the physical properties of the wire. Processing with intermediate anneals is acceptable when the requirements for physical properties of the wire permit reduced values. The conductivity of the hard-drawn wire is at least 57 percent IACS. If greater con-ductivity or increased elongation is desired, the wiremay be annealed or partially annealed after the desired wire size is ob-tained and cooled. Fully annealed wire has a conductivity ` ~6~t73~1 .
of at least 58 percent IACS. At the conclusion of the drawing operation and optional annealing op~ration, it is found that the alloy wire has the properties of improved tensile strength and yield strength together with improved thermal stability, percent ultimate elongation and in-creased ductility and fatigue resistance as specified previ-ously in this application. The annealing operation may be continuous as in resistance annealing, induction annealing, convection annealing by continuous furnaces or radiation annealing by continuous furnaces, or, preferably, may be batch annealed in a batch furnaceO When continuously annealing, temperatures of about 450F to about 1200F may be employed with annealing times of about five minutes to about 1/10,000 of a minute. Generally, however, continuous annealing temperatures and times may be adjusted to meet the xequiremenets of the particular overall processing operation so long as the desired physical properties are achieved. In a batchannealing operation, a temperature of approximately 400F to about 750F is employed with resi-,~, dence times of about thirty (30) minutes to about twenty-four (24) hours. As mentioned with respect to continuous annealing, in batch annealing the times and temperatures may be varied to suit the overall process so long as the desired physical properties are obtained.
It has been found that the properties of a No.
10 A.W.G. f~lly annealed soft wire of the present alloy vary between the following fig~lres:
Tensile ~ield Conductivity Strength psi Elongation Strength psi 58% - 63~ 12,000~24,000 12~ - 30%8,000-18,000 ~6~7~53 ~ more complete understanding of the invention will be obtained from the following example:
EXAMPLE NO. 1.
Various melts were prepared by adding the re-~uired amount of alloying elements to 1816 grams of molten aluminum, containing less than 0.10% trace element ~rities, to achieve a perc~ntage concentration of elements as shown in the accompanying table; the remainder being aluminum.
Graphite crucibles are used except in those cases where khe alloying elements are known carbide formers, in which cases aluminum oxide crucibles are used. The melts are held for sufficient times and at sufficient temperatures to allow o plete solubility of the alloying elements with the base aluminum. An argon atmosphere is provided over the melt ~o provide oxidation. Each melt is continuously cast on a con tinuous casting machine and immediately hot-roll~d through a rolling mill to 3/8 inch continuous rod. The hard rod was then cold drawn, without any preliminary or immediate anneals, into 0~1019 inch, 10 gauge A.W.G. wire. The wire was then given a final anneal for five hours at 650F resulting in soft wire.
The types of alloys employed and the results of the tests performed thereon are as follows:
TABLE 1.
; Ni Fe UTS % Elong. ~ IACS
_ .30 1.00 17,500 12.5 60.40 .80 .70 18,300 25.6 59.73 1.00 .60 17,900 26.1 59.97 . ~
1.50 .40 17,800 24.8 ~3.52 ~ r___;~ ~1 ....... . . . . _.. _ _ , _ _ _ __ _ ~ 11 ~
of elements which improve phy~ical properties without substantially lessening conductivity will yield an acceptable and useful product.
In applicant's prior Canadian Patent ApplicationSerial No. 143~514, Filed May 31J 1972, there is disclosed a new aluminum alloy electrical con-ductor which was formulated to yield improved physical properties with acceptable electrical conductivity. The aluminum base alloy was prepared by mixing nickel, iron and optionally other alloying elements with aluminum in a furnace to obtain a melt having requisite percen*ages of elements. It was found that suitable results were obtained with nickel present in a weight percentage of from about 0.20 percent to about 1.60 percent. Superior results were achieved when nickel was present in a weight percentage of from about 0.50 percent to about 1.00 percent and particularly superior and preferred results were obtained when nickel was present in a percentage by weight of from about 0.60 percent to about 0.80 percent.
Suitable results were obtained with iron present in a weight percentage of from about 0.30 percent to about 1.30 percent. Superior results were achieved when iron was present in a weight percentage of from about 0.40 percent to about 0.80 percent and particularly superior and preferred results were obtained when iron was present in a percentage by weight of from about 0.45 percent to about 0.65 percent.
The aluminum content of the alloy of the afore mentioned patent document could vary from about 97.00 per-cent to about 99.50 percent by weight with superior resultsbeing obtained with the aluminum content between about 97.~0% and about 99.20% by weight. Since the percentage for maximum and minimum aluminum did not correspond with the maximums and minimums for alloying elements, it was apparent that suitable results were not obtained if the ma~imum percentages for all alloying elements were employed. If commercial aluminum was employed in preparing the melt, it was preferred that the aluminum prior to adding to the melt in the furnace, contain no more than 0.10 percent total of trace impurities.
Optionally the alloy of the aforementioned patent document could contain an additional alloying element or group of alloying elements. The total concentration of the optional alloying elements could be up to about 2.00 percent by weight; preferably from about 1.10 percent to about 1.50 percent by weight. Particularly superior and preferred results were obtained when from about 0.10 percent to about 1.00 percent by weight of total additional alloying elements was employed; particularly if at least one element is selected from the sub group of magnesium, niobium, tantalum, silicon and zirconium.
Additional alloying elements included the following:
ADDITIONAL ALLOYING ELEMENTS
.
Magnesium Cesium Dysprosium Cobalt ~ttrium Terbium Copper Scandium Erbium Silicon Thorium Neodynium Zirconium Tin Indium Cerium Zinc Boron a~
Niobium Bismuth Thallium Hafnium Antimony Rubidium Lanthanum Vanadium ~itanium Tantalum Rhenium Carkon Other elements could be present in trace amounts provided that they did not adversely affect the mechanical, electrical and physical properties of the product.
Superior results were obtained with the following additional elements:
PREFERRED ADDITIONAL ALLOY:l:NG ELEMENTS
Magnesium Zirconium Scandium Cobalt Niobium Thorium Copper Tantalum Rare Earth Metals Silicon Yttrium Carbon Particularly superior and preferred results were obtained with the use of cobalt or magnesium as the additional alloying element. Suitable results were obtained with magnesium or cobalt in a percentage range of from about 0.001% to about 1.00~ by weight with superior results being obtained when from about 0.025% to about 0.50~ by weight was used. Particularly superior and preferred results were obtained when from about 0.03% ko about 0.10% by weight of magnesium or cobalt was employed.
While the method of the aforementioned patent specification yielded an aluminum alloy electrical conductor product having improved physical properties as compared with conventional EC aluminum alloy conductors, while main-~6~'73~3 taining comparable electrical conductivityj it did nothave sufficient ductility to facilitate the continuous processing steps, nor to yield a finished wire product having satisfactory elongation characteristics. In par-ticular, the cast bar would tend to split and crack durinc the continuous rolling and cold-drawing thereof, and the wire product often contained intermetallic compound pre-cipitates which, subsequent to cold-drawing of the product, exhibited an insufficient ductility.
STATEMENT OF THE INVENTION
In view of the foregoing, it should be apparent that a need still exists in the art for a method of preparing an aluminum alloy conductor that will improve the ductility of the product manufactured by the process of the aforementioned patent specification, so that such product can be continuously rolled and cold-drawn without splitting and cracking,and so that the wire product will have an elongation of at least 12~ when measured as a No. 10 A.W.G. wire in the fully annealed condition.
In order to accomplish the foregoing, it has been determined in accordance with this invention that the additional alloying elements specified in the aforementioned patent specification must be very closely controlled, with-in predetermined limits, specifically the copper, magnesium and silicon. Thus, there is provided in accordance with this invention a method of preparing an aluminum alloy conductor having a minimum conductivity of at least 58 percent IACS, good thermal stability, a tensile strength of 73~
at least 12,000 psi, and a yield strength of at least 8,000 psi when measured as a fully annealed wire, comprising:
(a) Alloying from 0.20 to 1.60 weight percent nickel, from 0.30 to 1.30 weight percent iron, up to a total of 2.00 wPight percent of additional alloying elements including copper, magnesium and silicon, and from about 97.00 to about 99.50 weigbt percent aluminum with associated trace elements;
(b) Casting the alloy in a moving mold formed between a groove in the periphery of a rotating casting wheel and a metal belt lying adjacent said groove for a portion of its length;
(c) Hot rolling the cast alloy substan-tially immediately after casting while the cast alloy is in substantially that condition as cast to form a continuous rod; and (d~ Drawing the rod through wire-drawing dies, without any preliminary or intermediate anneals between dies, to form wire of finish gauge size;
characterized in that in order to improve the ductility of the product the copper content of the alloy is maintained at less than 0.~5 weight percent, thereby inhibiting the formation of cuprous oxide particles and thus permitting continuous rolling and drawing without splitting and cracking of the product.
The present invention is further characterized in that in order to further improve the ductility of the product the magnesium content of the alloy i5 maintained ~ :lt6~3~3 at les than 0.1 weight percent whan the silicon exceeds 0.15 weight percent, thereby yi~lding a wire having an elongation of at least 12 percent when measured as a No. lO A.W.G. wire in the fully annealed condition.
As expressed above, it has heen determined in accordance with this invention that the copper content must be very closely controlled, within the range specified above, in order to permit continuous processing of the product. Although copper is an effective hardening element, if more than 0.05% copper is present in the alloy of this invention, it will form extremely hard cuprous oxide par-ticles that will result in splitting and cracking when the continuously processed product is rolled and cold drawn.
Since a conventionally processed product can be homogenized prior to rolling to refine the grain structure, the copper content thereof need not be so closely controlled. However, when the product is continuously processed in accordance with the instant invention, the cast bar is substantially immediately rolled in the as-cast condition and thus does not have the benefit of an homogenizing step. Consequently, the copper content o~ the alloy must be closely controlled to avoid the brittleness which leads to splitting and crack-ing of the bar when processed according to the method of this invention.
Similarly, as expressed above, it has been determined in accordance with this invention that the sili-con and magnesium contents must also be very closely controlled. In particular, when the silicon exceeds 0.15 percent, the magnesium must be limited to less than 0.1 ~36~73~
percent; ot~erwise, the product w~ll exhibit an insufficient ductility subsequent to cold drawing, if the product was previously con~inuously cast and rolled.
After preparing the melt in the manner des-cribed in the aforementioned patent specification, with the copper, magnesium and silicon controlled in accordance with the present invention, the aluminum alloy is continuously cast into a continuous bar by a continuous casting machine and then substantially immediately thereafter, hot-worked in a rolling mill to yield a continuous aluminum alloy rod.
An example of a continuous casting and rolling operation capable of producing continuous rod as specified in this application is disclosed in the aforementioned patent speci-fication.
To produce wire of various gau~es, the continuous rod produced by the casting and rolling operation is processed in a reduction operation. The unannealed rod (i.e., as rolled to f temper) is cold-drawn through a series of progressively constricted dies, without preliminary or intermediate anneals, to ~orm a continuous wire of desired diameter. It has been found that the elimination of intermediate anneals improves the physical properties of the wire. Processing with intermediate anneals is acceptable when the requirements for physical properties of the wire permit reduced values. The conductivity of the hard-drawn wire is at least 57 percent IACS. If greater con-ductivity or increased elongation is desired, the wiremay be annealed or partially annealed after the desired wire size is ob-tained and cooled. Fully annealed wire has a conductivity ` ~6~t73~1 .
of at least 58 percent IACS. At the conclusion of the drawing operation and optional annealing op~ration, it is found that the alloy wire has the properties of improved tensile strength and yield strength together with improved thermal stability, percent ultimate elongation and in-creased ductility and fatigue resistance as specified previ-ously in this application. The annealing operation may be continuous as in resistance annealing, induction annealing, convection annealing by continuous furnaces or radiation annealing by continuous furnaces, or, preferably, may be batch annealed in a batch furnaceO When continuously annealing, temperatures of about 450F to about 1200F may be employed with annealing times of about five minutes to about 1/10,000 of a minute. Generally, however, continuous annealing temperatures and times may be adjusted to meet the xequiremenets of the particular overall processing operation so long as the desired physical properties are achieved. In a batchannealing operation, a temperature of approximately 400F to about 750F is employed with resi-,~, dence times of about thirty (30) minutes to about twenty-four (24) hours. As mentioned with respect to continuous annealing, in batch annealing the times and temperatures may be varied to suit the overall process so long as the desired physical properties are obtained.
It has been found that the properties of a No.
10 A.W.G. f~lly annealed soft wire of the present alloy vary between the following fig~lres:
Tensile ~ield Conductivity Strength psi Elongation Strength psi 58% - 63~ 12,000~24,000 12~ - 30%8,000-18,000 ~6~7~53 ~ more complete understanding of the invention will be obtained from the following example:
EXAMPLE NO. 1.
Various melts were prepared by adding the re-~uired amount of alloying elements to 1816 grams of molten aluminum, containing less than 0.10% trace element ~rities, to achieve a perc~ntage concentration of elements as shown in the accompanying table; the remainder being aluminum.
Graphite crucibles are used except in those cases where khe alloying elements are known carbide formers, in which cases aluminum oxide crucibles are used. The melts are held for sufficient times and at sufficient temperatures to allow o plete solubility of the alloying elements with the base aluminum. An argon atmosphere is provided over the melt ~o provide oxidation. Each melt is continuously cast on a con tinuous casting machine and immediately hot-roll~d through a rolling mill to 3/8 inch continuous rod. The hard rod was then cold drawn, without any preliminary or immediate anneals, into 0~1019 inch, 10 gauge A.W.G. wire. The wire was then given a final anneal for five hours at 650F resulting in soft wire.
The types of alloys employed and the results of the tests performed thereon are as follows:
TABLE 1.
; Ni Fe UTS % Elong. ~ IACS
_ .30 1.00 17,500 12.5 60.40 .80 .70 18,300 25.6 59.73 1.00 .60 17,900 26.1 59.97 . ~
1.50 .40 17,800 24.8 ~3.52 ~ r___;~ ~1 ....... . . . . _.. _ _ , _ _ _ __ _ ~ 11 ~
3~
% Elong. = Percent Ultimate Elongation UTS - Ultimate Tensile Strength % IACS = Conductivity EX~MPLE NO. 2.
An additional alloy melt was pxepared accord-: ing to Example No. 1 so that the composition was as follows in weight percent:
Nickel - 0.60%
Iron - 0.90%
Magnesium - 0.15~
Aluminum - Remainder The melt was processed to a No. 10 gauge soft wire. The . physical properties of the wire were as follows:
;~~ Ultimate Tensile Strength - 18,200 psi ~'! Percent Ultimate E:Longation - 25.2%
Conductivity - 59.10% IACS
EXAMPLE NO~ 3.
An additional alloy melt was prepared according to Example No. 1 so that the composition was as follows in weight percent:
Nickel - 0.40%
Iron - 1.10%
Aluminum - Remainder . The melt was processed to a No. 10 gauge soft wire. The physical properties of the wire were as follows:
Ultimate Tensile Strength - 17,400 psi Percent Ultimate Elongation - 14.1%
Conductivity - 60.30% IACS
' ~6~
EXAMPLE NO. 4.
An additional ~lloy melt was prepared accord-ing to Example ~o. 1 so that the composition was as follows in weight percent:
Nickel - 1.60~
Iron - 0.30%
Aluminum - Remainder The melt was processed to a No. 10 gauge soft wire. The physical propertie~ of the wire were as follows:
Ultimate Tensîle Strength - 17,200 psi Percent Ultimate Elongation - 27.5%
Conductivity - 59.1% IACS
EXAMPLE NO. 5.
~ An additional alloy melt was prepared accord-: ing to Example No. 1 so that the composition was as follows in weight percent:
~ Nickel - 0.20%
: Iron - 1.30%
Aluminum - Remainder ,~
The melt was processed to a No. 10 gauge soft wire. The physical properties of the wire were as follows:
: Ultimate Tensile Strength - 17,500 psi Percent Ultimate Elongation - 13.5%
Conductivity - 61.05% IACS
EXAMPLE NO. 6.
; An additional alloy melt was prepared accord-ing to Example No. 1 so that the composition was as follows in weight percent:
6~
Nickel - 0.80%
Iron - 0.45~
Cobalt - 0.10%
Aluminum ~ Remainder The melt was processed to a No. 10 gaug~ soft wire. The physical properties of the wire were as ~ollows:
Ultimate Tensile Strength - 17,850 psi Percent Ultimate Elongation - 23.6%
; Conductivity - 59.8 IACS
Thxough testing and analysis of an alloy containing 0.80 weight percent nickel, 0.30 weight percent iron, and the remainder aluminum, it has been found that the present aluminum base alloy after cold working includes intermetallic compound precipitates. One of the compounds is identified as nickel aluminate (NiA13) and the other is identified as iron aluminate (FeA13). The nickel inter-metallic compound is found to be very stable and e~pecially so at high temperatures. The nickel compound also has a .1 low tendency to coalesce during annealing of products formed from the alloy and the compound is generally inco-herent with the aluminum matrix. The mechanism of strength-ening for this alloy is in par~ due to the dispersion of the nickel intermetallic compound as a precipitate throughout the aluminum matrix. The precipitate tends to pin disloca-tion sites which are created during cold working of the wire formed from the alloy. Upon examination of the nickel intermetallic compound precipitate in a cold drawn wire, it is found that the precipitates are oriented in the direction ., of drawing. In addition, it is found that the precipitates gl'73~
can be rod-like, plate-like, or spherical in configuration.
Other intermetallic compounds may also be formed depending upon the corstituents of the melt and the relative concentrations of the alloying elements. Those intermetallic compounds include the following: Ni2A13, 2 5~ Co2Alg, Co4A113, CeA14, CeA12, VAlll, VA17, VA16, Val3, Vall2, Zr3Al, Zr2Al, LaA14, A13Ni2, A12Fe5, Fe3NiA110, Co2A15, FeNiAlg.
The iron aluminate intermetallic compound also contributes to the pinning of dislocation sites during cold working of the wire. Upon examination of the iron inter-metallic compound precipitate in a cold drawn wire, it is found that the precipitates are substantially evenly dis-tributed through the alloy and have a particle size of less than 1 micron. If the wire is drawn without any inter-mediate anneals, the particle size of the iron intermetallic compounds is less than 2,000 angstroms.
A charact~ristic of high conductivity aluminum alloy wires which is not indicated by the historical tests for tensile strength, percent elongation and electrical conductivity is the possible change in properties as a result of increases, decreases, or fluctuations of the tem-perature of ~he strands. It is apparent that the maximum operating temperature of a strand or series of strands will be affected by this temperature characteristic. The charac-teristic is also quite significant from a manufacturing viewpoint since many insulation processes require high temperature thermal cures.
It has been found that the aluminum alloy wire of the present invention has a characteristic of thermal stability which exceeds the thermal stability of convention-al aluminum alloy wires.
For the purpose of clarity/ the following terminology used in this application is explained as follows:
Aluminum alloy rod - A solid product that is long in relation to its cross-section. Rod normally has a cross-section of between three inches and 0.375inches.
Aluminum alloy wire - A solid wrought product that is long in relation to its cross-section, which is square or rectangular with sharp or rounded corners or edges, or is round, a regular hexagon or a regular octagon, and whose diameter or greatest perpendicular distance between parallel faces is between 0.374 inches and 0.0031 inches.
While this invention has been described in detail with particu].ar reference to preferred embodiments thereof, it will be understood that variations and modifi- -cations can be effected within the spirit and scope of the invention as described hereinbefore and as defined in the appended claimS.
., ,~ .
% Elong. = Percent Ultimate Elongation UTS - Ultimate Tensile Strength % IACS = Conductivity EX~MPLE NO. 2.
An additional alloy melt was pxepared accord-: ing to Example No. 1 so that the composition was as follows in weight percent:
Nickel - 0.60%
Iron - 0.90%
Magnesium - 0.15~
Aluminum - Remainder The melt was processed to a No. 10 gauge soft wire. The . physical properties of the wire were as follows:
;~~ Ultimate Tensile Strength - 18,200 psi ~'! Percent Ultimate E:Longation - 25.2%
Conductivity - 59.10% IACS
EXAMPLE NO~ 3.
An additional alloy melt was prepared according to Example No. 1 so that the composition was as follows in weight percent:
Nickel - 0.40%
Iron - 1.10%
Aluminum - Remainder . The melt was processed to a No. 10 gauge soft wire. The physical properties of the wire were as follows:
Ultimate Tensile Strength - 17,400 psi Percent Ultimate Elongation - 14.1%
Conductivity - 60.30% IACS
' ~6~
EXAMPLE NO. 4.
An additional ~lloy melt was prepared accord-ing to Example ~o. 1 so that the composition was as follows in weight percent:
Nickel - 1.60~
Iron - 0.30%
Aluminum - Remainder The melt was processed to a No. 10 gauge soft wire. The physical propertie~ of the wire were as follows:
Ultimate Tensîle Strength - 17,200 psi Percent Ultimate Elongation - 27.5%
Conductivity - 59.1% IACS
EXAMPLE NO. 5.
~ An additional alloy melt was prepared accord-: ing to Example No. 1 so that the composition was as follows in weight percent:
~ Nickel - 0.20%
: Iron - 1.30%
Aluminum - Remainder ,~
The melt was processed to a No. 10 gauge soft wire. The physical properties of the wire were as follows:
: Ultimate Tensile Strength - 17,500 psi Percent Ultimate Elongation - 13.5%
Conductivity - 61.05% IACS
EXAMPLE NO. 6.
; An additional alloy melt was prepared accord-ing to Example No. 1 so that the composition was as follows in weight percent:
6~
Nickel - 0.80%
Iron - 0.45~
Cobalt - 0.10%
Aluminum ~ Remainder The melt was processed to a No. 10 gaug~ soft wire. The physical properties of the wire were as ~ollows:
Ultimate Tensile Strength - 17,850 psi Percent Ultimate Elongation - 23.6%
; Conductivity - 59.8 IACS
Thxough testing and analysis of an alloy containing 0.80 weight percent nickel, 0.30 weight percent iron, and the remainder aluminum, it has been found that the present aluminum base alloy after cold working includes intermetallic compound precipitates. One of the compounds is identified as nickel aluminate (NiA13) and the other is identified as iron aluminate (FeA13). The nickel inter-metallic compound is found to be very stable and e~pecially so at high temperatures. The nickel compound also has a .1 low tendency to coalesce during annealing of products formed from the alloy and the compound is generally inco-herent with the aluminum matrix. The mechanism of strength-ening for this alloy is in par~ due to the dispersion of the nickel intermetallic compound as a precipitate throughout the aluminum matrix. The precipitate tends to pin disloca-tion sites which are created during cold working of the wire formed from the alloy. Upon examination of the nickel intermetallic compound precipitate in a cold drawn wire, it is found that the precipitates are oriented in the direction ., of drawing. In addition, it is found that the precipitates gl'73~
can be rod-like, plate-like, or spherical in configuration.
Other intermetallic compounds may also be formed depending upon the corstituents of the melt and the relative concentrations of the alloying elements. Those intermetallic compounds include the following: Ni2A13, 2 5~ Co2Alg, Co4A113, CeA14, CeA12, VAlll, VA17, VA16, Val3, Vall2, Zr3Al, Zr2Al, LaA14, A13Ni2, A12Fe5, Fe3NiA110, Co2A15, FeNiAlg.
The iron aluminate intermetallic compound also contributes to the pinning of dislocation sites during cold working of the wire. Upon examination of the iron inter-metallic compound precipitate in a cold drawn wire, it is found that the precipitates are substantially evenly dis-tributed through the alloy and have a particle size of less than 1 micron. If the wire is drawn without any inter-mediate anneals, the particle size of the iron intermetallic compounds is less than 2,000 angstroms.
A charact~ristic of high conductivity aluminum alloy wires which is not indicated by the historical tests for tensile strength, percent elongation and electrical conductivity is the possible change in properties as a result of increases, decreases, or fluctuations of the tem-perature of ~he strands. It is apparent that the maximum operating temperature of a strand or series of strands will be affected by this temperature characteristic. The charac-teristic is also quite significant from a manufacturing viewpoint since many insulation processes require high temperature thermal cures.
It has been found that the aluminum alloy wire of the present invention has a characteristic of thermal stability which exceeds the thermal stability of convention-al aluminum alloy wires.
For the purpose of clarity/ the following terminology used in this application is explained as follows:
Aluminum alloy rod - A solid product that is long in relation to its cross-section. Rod normally has a cross-section of between three inches and 0.375inches.
Aluminum alloy wire - A solid wrought product that is long in relation to its cross-section, which is square or rectangular with sharp or rounded corners or edges, or is round, a regular hexagon or a regular octagon, and whose diameter or greatest perpendicular distance between parallel faces is between 0.374 inches and 0.0031 inches.
While this invention has been described in detail with particu].ar reference to preferred embodiments thereof, it will be understood that variations and modifi- -cations can be effected within the spirit and scope of the invention as described hereinbefore and as defined in the appended claimS.
., ,~ .
Claims (17)
1. A method of preparing an aluminum alloy conductor having a minimum conductivity of at least 58 percent IACS, good thermal stability, a tensile strength of at least 12,000 psi, and a yield strength of at least 8,000 psi when measured as a fully annealed wire, comprising:
(a) Alloying from 0.20 to 1.60 weight percent nickel, from 0.30 to 1.30 weight percent iron, up to a total of 2.00 weight percent of additional alloying elements at least one element from the group consisting of copper, magnesium, silicon, niobium, tantalum and zirconium and from about 97.00 to about 99.50 weight percent aluminum with associated trace elements;
(b) Casting the alloy in a moving mold formed between a groove in the periphery of a rotating casting wheel and a metal belt lying adjacent said groove for a portion of its length;
(c) Hot rolling the cast alloy substantially immediately after casting while the cast alloy is in substantially that condition as cast to form a continuous rod; and (d) Drawing the rod through wire-drawing dies, without any preliminary of intermediate anneals between dies, to form wire of finish gauge size;
characterized in that in order to improve the ductility of the product the copper content of the alloy is maintained at less than 0.05 weight percent, particles and thus permitting continuous rolling and drawing without splitting and cracking of the product.
(a) Alloying from 0.20 to 1.60 weight percent nickel, from 0.30 to 1.30 weight percent iron, up to a total of 2.00 weight percent of additional alloying elements at least one element from the group consisting of copper, magnesium, silicon, niobium, tantalum and zirconium and from about 97.00 to about 99.50 weight percent aluminum with associated trace elements;
(b) Casting the alloy in a moving mold formed between a groove in the periphery of a rotating casting wheel and a metal belt lying adjacent said groove for a portion of its length;
(c) Hot rolling the cast alloy substantially immediately after casting while the cast alloy is in substantially that condition as cast to form a continuous rod; and (d) Drawing the rod through wire-drawing dies, without any preliminary of intermediate anneals between dies, to form wire of finish gauge size;
characterized in that in order to improve the ductility of the product the copper content of the alloy is maintained at less than 0.05 weight percent, particles and thus permitting continuous rolling and drawing without splitting and cracking of the product.
2. The method according to claim 1, characterized in that in order to further improve the ductility of the product the magnesium content of the alloy is maintained at less than 0.1 weight percent when the silicon exceeds 0.15 weight percent, thereby yielding a wire having an elongation of at least 12 percent when measured as a No. 10 A.W.G. wire in the fully annealed condition.
3. The method according to claim 1 characterized that in preferred from the nickel and iron are alloyed with aluminum in the following proportions:
Nickel - 0.60% to 0.80% by weight Iron - 0.45% to 0.65% by weight
Nickel - 0.60% to 0.80% by weight Iron - 0.45% to 0.65% by weight
4. The method according to claim 2 characterized that in preferred from the nickel and iron are alloyed with aluminum in the following proportions:
Nickel - 0.60% to 0.80% by weight Iron - 0.45% to 0.65% by weight.
Nickel - 0.60% to 0.80% by weight Iron - 0.45% to 0.65% by weight.
5. The method according to claim 1, characterized in that the alloying step includes the further addition of from 0.10 to about 1.00 weight percent of alloying elements selected from the group consisting of magnesium, niobium, tantalum, silicon and zirconium.
6. A method of preparing an aluminum alloy conductor having a minimum conductivity of at least 58 percent IACS, good thermal stability, a tensile strength of at least 12,000 psi, and a yield strength of at least 8,000 psi when measured as a fully annealed wire, comprising:
(a) Alloying from 0.20 to 1.60 weight percent nickel, from 0.30 to 1.30 weight percent iron, from 0.10 to about 1.00 weight percent alloying the elements at least one element selected from the group consisting of magnesium, niobium, tantalum, silicon and zirconium, and up to a total of 2.0 weight percent of secondary alloying elements at least one element from the group consisting of copper, magnesium and silicon, and from about 97.00 to about 99.50 weight percent aluminum with associated trace elements;
(b) Casting the alloy in a moving mold formed between a groove in the periphery of a rotating casting wheel and a metal belt lying adjacent said groove for a portion of its length;
(c) Hot rolling the cast alloy substantially immediately after casting while the cast alloy is in substantially that condition as cast to form a continuous rod; and (d) Drawing the rod through wire-drawing dies, without any preliminary of intermediate anneals between dies, to form wire of finish gauge size;
characterized in that order to improve the ductility of the product the copper content of the alloy is maintained at less than 0.05 weight percent, thereby inhibiting the formation of cuprous oxide particles and thus permitting continuous rolling and drawing without splitting and cracking of the product.
(a) Alloying from 0.20 to 1.60 weight percent nickel, from 0.30 to 1.30 weight percent iron, from 0.10 to about 1.00 weight percent alloying the elements at least one element selected from the group consisting of magnesium, niobium, tantalum, silicon and zirconium, and up to a total of 2.0 weight percent of secondary alloying elements at least one element from the group consisting of copper, magnesium and silicon, and from about 97.00 to about 99.50 weight percent aluminum with associated trace elements;
(b) Casting the alloy in a moving mold formed between a groove in the periphery of a rotating casting wheel and a metal belt lying adjacent said groove for a portion of its length;
(c) Hot rolling the cast alloy substantially immediately after casting while the cast alloy is in substantially that condition as cast to form a continuous rod; and (d) Drawing the rod through wire-drawing dies, without any preliminary of intermediate anneals between dies, to form wire of finish gauge size;
characterized in that order to improve the ductility of the product the copper content of the alloy is maintained at less than 0.05 weight percent, thereby inhibiting the formation of cuprous oxide particles and thus permitting continuous rolling and drawing without splitting and cracking of the product.
7. The method according to claim 1, characterized in that the alloy step includes the addition of magnesium in an amount sufficient to yield an alloy having the following weight percentages:
Nickel - 0.60% to 0.80%
Iron - 0.45% to 0.65%
Magnesium - 0.03% to 0.10%
Aluminum - remainder.
Nickel - 0.60% to 0.80%
Iron - 0.45% to 0.65%
Magnesium - 0.03% to 0.10%
Aluminum - remainder.
8. The method according to claim 2, characterized in that the alloy step includes the addition of magnesium in an amount sufficient to yield an alloy having the following weight percentages:
Nickel - 0.60% to 0.80%
Iron - 0.45% to 0.65%
Magnesium - 0.03% to 0.10%
Aluminum - remainder.
Nickel - 0.60% to 0.80%
Iron - 0.45% to 0.65%
Magnesium - 0.03% to 0.10%
Aluminum - remainder.
9. The method according to claim 4, characterized in that the alloy step includes the addition of magnesium in an amount sufficient to yield an alloy having the following weight percentages:
Nickel - 0.60% to 0.80%
Iron - 0.45% to 0.65%
Magnesium - 0.03% to 0.10%
Aluminum - remainder.
Nickel - 0.60% to 0.80%
Iron - 0.45% to 0.65%
Magnesium - 0.03% to 0.10%
Aluminum - remainder.
10. The method according to claim 1 characterized in that the alloying step includes the addition of niobium and tantalum in an amount sufficient to yield an alloy having the following weight percentages:
Nickel - 0.60%
Iron - 0.65 Niobium - 0.30%
Tantalum - 0.18%
Aluminum - remainder.
Nickel - 0.60%
Iron - 0.65 Niobium - 0.30%
Tantalum - 0.18%
Aluminum - remainder.
11. The method according to claim 4 characterized in that the alloying step includes the addition of niobium and tantalum in an amount sufficient to yield an alloy having the following weight percentages:
Nickel - 0.60%
Iron - 0.65%
Niobium - 0.30%
Tantalum - 0.18%
Aluminum - remainder.
Nickel - 0.60%
Iron - 0.65%
Niobium - 0.30%
Tantalum - 0.18%
Aluminum - remainder.
12. The method according to claim 1 characterized in that the alloying step includes the addition of zirconium in an amount sufficient to yield an alloy having the following weight percentages:
Nickel - 0.80%
Iron - 0.45%
Zirconium - 0.60%
Aluminum - remainder.
Nickel - 0.80%
Iron - 0.45%
Zirconium - 0.60%
Aluminum - remainder.
13. The method according to claim 4 characterized in that the alloying step includes the addition of zirconium in an amount sufficient to yield an alloy having the following weight percentages:
Nickel - 0.80%
Iron - 0.45%
Zirconium - 0.60%
Aluminum - remainder.
Nickel - 0.80%
Iron - 0.45%
Zirconium - 0.60%
Aluminum - remainder.
14. An aluminum alloy electrical conductor, manufactured according to the method of claims 1, 2, or 3, and having a minimum conductivity of 58% IACS, an ultimate tensile strength of at least 12,000 PSI, a yield strength of at least 8000 PSI and an elongation of at least 12% when measured is a No. 10 A.W.G. wire in the fully annealed condition.
15. An aluminum alloy electrical conductor, manufactured according to the method of claims 4, 5, or 6, and having a minimum conductivity of 58% IACS, an ultimate tensile strength of at least 12,000 PSI, a yield strength of at least 8000 PSI and an elongation of at least 12% when measured is a No. 10 A.W.G. wire in the fully annealed condition.
16. An aluminum alloy electrical conductor, manufactured according to the method of claims 7, 8, or 9, and having a minimum conductivity of 58% IACS, an ultimate tensile strength of at least 12,000 PSI, a yield strength of at least 8000 PSI and an elongation of at least 12% when measured is a No. 10 A.W.G. wire in the fully annealed condition.
17. An aluminum alloy electrical conductor, manufactured according to the method of claims 10, 11 or 12, and having a minimum conductivity of 58% IACS, an ultimate tensile strength of at least 12,000 PSI, a yield strength of at least 8000 PSI and an elongation of at least 12% when measured is a No. 10 A.W.G. wire in the fully annealed condition.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US05/639,077 US4080222A (en) | 1974-03-01 | 1975-12-09 | Aluminum-iron-nickel alloy electrical conductor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1064738A true CA1064738A (en) | 1979-10-23 |
Family
ID=24562638
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA266,950A Expired CA1064738A (en) | 1975-12-09 | 1976-12-01 | Aluminum-iron-nickel alloy electrical conductor |
Country Status (9)
| Country | Link |
|---|---|
| JP (1) | JPS5271322A (en) |
| CA (1) | CA1064738A (en) |
| DE (1) | DE2655433A1 (en) |
| ES (1) | ES454100A1 (en) |
| FR (1) | FR2335020A1 (en) |
| GB (1) | GB1510940A (en) |
| MX (1) | MX3842E (en) |
| NO (1) | NO146715C (en) |
| SE (1) | SE7613811L (en) |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4845543A (en) * | 1983-09-28 | 1989-07-04 | Hitachi, Ltd. | Semiconductor device and method of manufacturing the same |
| IT1183375B (en) * | 1984-02-24 | 1987-10-22 | Hitachi Ltd | SEMICONDUCTOR DEVICE INCLUDING A BALL, CONDUCTING WIRES AND EXTERNAL CONDUCTING PORTIONS ARE CONNECTED TO THE BALL THROUGH SUCH CONDUCTING WIRES |
| FR2566182B1 (en) * | 1984-02-24 | 1988-01-08 | Hitachi Ltd | SEMICONDUCTOR DEVICE |
| CN1272805C (en) | 2002-06-28 | 2006-08-30 | 住友精密工业株式会社 | Conductor for movable electric circuit and vibration type gyro |
| CN104264003B (en) * | 2014-09-26 | 2016-09-07 | 国网河南省电力公司周口供电公司 | A kind of energy-saving aluminium alloy wire of stretch-proof and preparation method thereof |
| CN104233010A (en) * | 2014-09-29 | 2014-12-24 | 国网河南省电力公司周口供电公司 | Aluminum alloy lead with high conductivity and preparation method of aluminum alloy lead |
| CN104532070A (en) * | 2014-12-23 | 2015-04-22 | 合肥派成铝业有限公司 | Aluminum alloy with excellent processing performance for doors and windows |
| CN104681120B (en) * | 2015-03-06 | 2017-06-13 | 广州臣泰电子科技有限公司 | A kind of composite high pressure conductor material and preparation method thereof |
| CN104674071B (en) * | 2015-03-06 | 2016-11-16 | 吴江华诚复合材料科技有限公司 | A kind of aluminum alloy materials and preparation method thereof |
| CN105506406A (en) * | 2016-01-27 | 2016-04-20 | 东莞佛亚铝业有限公司 | High-conductivity aluminum alloy wire and preparing method thereof |
| CN114672702B (en) * | 2022-05-27 | 2023-01-31 | 江苏中天科技股份有限公司 | Super heat-resistant aluminum alloy monofilament |
-
1976
- 1976-11-30 GB GB49816/76A patent/GB1510940A/en not_active Expired
- 1976-12-01 CA CA266,950A patent/CA1064738A/en not_active Expired
- 1976-12-06 NO NO764159A patent/NO146715C/en unknown
- 1976-12-07 DE DE19762655433 patent/DE2655433A1/en not_active Withdrawn
- 1976-12-07 FR FR7636773A patent/FR2335020A1/en active Pending
- 1976-12-08 SE SE7613811A patent/SE7613811L/en not_active Application Discontinuation
- 1976-12-09 JP JP51147212A patent/JPS5271322A/en active Pending
- 1976-12-09 ES ES454100A patent/ES454100A1/en not_active Expired
- 1976-12-09 MX MX765206U patent/MX3842E/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| NO146715B (en) | 1982-08-16 |
| NO764159L (en) | 1977-06-10 |
| FR2335020A1 (en) | 1977-07-08 |
| GB1510940A (en) | 1978-05-17 |
| DE2655433A1 (en) | 1977-06-16 |
| SE7613811L (en) | 1977-06-10 |
| MX3842E (en) | 1981-08-14 |
| ES454100A1 (en) | 1977-12-01 |
| JPS5271322A (en) | 1977-06-14 |
| NO146715C (en) | 1982-11-24 |
| AU2013176A (en) | 1978-06-08 |
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