US3394036A - Annealing titanium wire - Google Patents
Annealing titanium wire Download PDFInfo
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- US3394036A US3394036A US474764A US47476465A US3394036A US 3394036 A US3394036 A US 3394036A US 474764 A US474764 A US 474764A US 47476465 A US47476465 A US 47476465A US 3394036 A US3394036 A US 3394036A
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- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title description 32
- 238000000137 annealing Methods 0.000 title description 3
- 238000010438 heat treatment Methods 0.000 description 37
- 239000010936 titanium Substances 0.000 description 28
- 229910052719 titanium Inorganic materials 0.000 description 28
- 238000001816 cooling Methods 0.000 description 24
- 229910045601 alloy Inorganic materials 0.000 description 23
- 239000000956 alloy Substances 0.000 description 23
- 230000009467 reduction Effects 0.000 description 22
- 238000005336 cracking Methods 0.000 description 13
- 238000010622 cold drawing Methods 0.000 description 11
- 238000000034 method Methods 0.000 description 11
- 238000005098 hot rolling Methods 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 230000008569 process Effects 0.000 description 4
- 229910001069 Ti alloy Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000006698 induction Effects 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 238000005097 cold rolling Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 241000212254 Alternaria porri Species 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- -1 Titanium Metals Chemical class 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 244000309464 bull Species 0.000 description 1
- 230000008878 coupling Effects 0.000 description 1
- 238000010168 coupling process Methods 0.000 description 1
- 238000005859 coupling reaction Methods 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/04—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire
- B21C37/045—Manufacture of wire or bars with particular section or properties
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/004—Heating the product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/02—Drawing metal wire or like flexible metallic material by drawing machines or apparatus in which the drawing action is effected by drums
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C9/00—Cooling, heating or lubricating drawing material
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B2015/0028—Drawing the rolled product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
Definitions
- ABSTRACT OF THE DISCLOSURE Method of reducing the cross section of titanium and titanium base alloy wire which has been previously hot rolled at a temperature below its beta transes comprising heating the wire to a temperature between the beta transes and about 100 F. above the beta transes followed by cooling to below the beta transes and cold drawing.
- This invention relates to heat-treating wire and more particularly to annealing titanium or titanium base alloy wire to provide improved cold-rolling characteristics.
- Conventional wire processing involves first hot-rolling to form a relatively large diameter wire which is subsequently cold drawn, often with several passes, through a die to provide the desired finished diameter.
- the wire may be cold worked to finished diameter by passing through multiple circumferential rollers having grooved edges. Adjacent edges of the working rollers form a circular aperture so that the wire is worked down to provide the desired finished diameter by a rolling instead of a simple drawing operation.
- the process of this invention comprises heat-treating titanium and titanium alloy wire at a temperature above its beta transes to eliminate the crystal orientation imparted by previous hot-rolling at a temperature below its beta transes.
- This particular heating step I have discovered, particularly in the case of titanium alloys, must be carried out so that the wire is heated rapidly to the heat-treating temperature, and then preferably cooled rapidly to prevent the, formation of large-size beta grain structure.
- the wire When the wire is heattreated in this manner, being quickly raised to temperature and then quickly cooled, it can be reduced to final gauge through a roller type wire drawing machine to produce wire of circularity substantially improved over similar wire drawn without such heat-treatment, In addition, the ductility of the wire will be high so that its cross sectional area may be reduced by a substantial percentage in a single pass through the roller wheels without cracking or breaking of the wire.
- the wire is pulled through a set of edgegrooved rolls 18, these in the illustration being a set of three arranged around the wire at a radial angle of each to the other with their edge grooves 20 forming a circular aperture through which the wire 4 is pulled by action of bull block 22 actuated by a suitable motor (not shown).
- first set of a pair may advantageously reduce the wire and give it a curved-side triangle cross section or oval or other non-circular shape, with the second and final set of rolls providing a circular aperture to impart the desired circular cross section.
- the wire whose cross section is to be reduced by th method of this invention is characterized by having been previously worked at a temperature below its beta transes. It is common practice in wire manufacture to work commercially pure and alpha and alpha-beta type titanium base alloys in the alpha-beta field or alpha field because this provides easiest plastic deformation without raising the temperature of the material to a point where rapid oxidation and surface deterioration takes place. Moreover, working in the beta field will generally result in larger grains which are difiicult to break down in subsequent working at lower temperatures.
- the process of this invention is to be applied to wire whose latest prior working will have been hot-rolling at a temperature below its beta transes because this type of rolling apparently produces a detrimental crystal structure which affects subsequent cold-rolling when the wire is drawn through edge-grooved rolls.
- hot-rolling at such temperatures results in an orientation of the metal crystals so that subsequent deformation will not be uniform in all directions.
- the ease of deformation in a plane perpendicular to the length of the wire will not be uniform at various radial angles in this plane.
- edgegrooved rolls no matter how strongly built and precisely aligned to produce a circular orifice through which the wire is drawn, can be deformed elastically to some extent so that wire having preferred crystal orientation, when passing through such rolls, will not produce a truly circular or uniform reduced cross section wire.
- the wire should be heated to a temperature definitely above its beta transes temperature, which may be determined for commercially pure titanium or any of the alpha or alpha-beta type titanium base alloys by metallurgical methods well known in the art.
- the minimum time that the wire is maintained above its beta transes temperature is not critical, since apparently transformation takes place almost instantaneously; and once the wire has been raised to above its beta transes and subsequently cooled, the time above the beta transes temperature, even though but a few seconds, will be sufiicient to produce the desired transformation of the crystal structure. It is preferred to heat the wire to a temperature between its beta transes and 100 F.
- the heat treating temperature is between the beta transes temperature and about 50 F. above the beta transes. While the temperature should be sufficiently higher than the beta transes to insure complete transformation, it is not desirable to raise to excessive temperature since this inevitably results in increased time above the beta transes, and also results in a tendency towards formation of large beta grains.
- the time for the heat-treating step of this invention is extremely critical, and for alpha and alpha-beta type titanium base alloys the total elapsed time for heating the wire from room temperature to above its beta transes plus the time it is maintained above its beta transes should not be greater than one minute. Preferably for best results with wire of the recited titanium base alloys the time should not be more than 30 seconds. For comcient that the temperature be rapidly reduced, and to accomplish this, air cooling will produce a relatively fast and efficient reduction of wire temperature from its annealed temperature down to room temperature and particularly at least through the beta transes temperature.
- the wire After heat-treatment and subsequent cooling, the wire is cold drawn through a set of edge-grooved rolls to produce circular wire of substantially uniform diameter.
- Table 1 provides examples of heat-treating commercially pure titanium wire above its beta transes temperature and subsequently cold drawing this through two sets of nested edge grooved rolls to produce wire of improved circularity.
- the wire was of commercially pure, unalloyed titanium designated in the trade as Ti-SSA.
- the original ingot of the commercially pure titanium was worked down through various stages, the wire being rolled on a hot mill starting at a temperature of about ]750 F. and finishing at a temperature of about 1300 F. The latest prior working (at 1300 F.) was in the alpha field.
- Table 1 shows the heat-treatment prior to drawing through the edge-grooved rolls, the starting diameter of the wire, which was measured as maximum and minimum diameters along a 10-foot length of wire, and also the diameter measured in the same manner after cold drawing through the edgegrooved rolls.
- the short time requirements for the heat-treating step of this invention requires means for heating wire very rapidly to high temperature. This can readily be accomplished by resistance heating or induction heating.
- resistance heating heavy electrical currents are passed through a limited section of the wire, and the current flow results in extremely rapid heating of the wire. It is no problem to raise the wire temperature to above its beta transes temperature in a matter of seconds when passing a sufficient amount of current.
- induction heating the wire is subjected to high frequency induced electric current, and this also will raise the temperature of the wire extremely rapidly; and raising to above the beta transes by induction heating can be accomplished well within the time limits hereinbefore recited.
- coils of wire When heattreating commercially pure titanium wire, and for which the time is not so critical, coils of wire may be furnace heat-treated, which takes appreciably longer than the other two methods suggested, but total heat-treating time may still be maintained within a desirable period under an hour.
- the heat-treated wire Once the heat-treated wire has been raised to above its beta transes temperature, it is then quickly cooled, at least down through its beta transes. This may be accomplished by any convenient means providing a relatively rapid cooling. Quenching, which involves submerging the hot wire in water or oil and results in an almost instantaneous cooling, can be employed, if desired, although such a fast cooling effect is not essential to satisfactory results according to this invention. It is sufii- It will be seen from Table 1 that with a heat-treatment below the beta transes with subsequent rapid cooling, the variation in wire diameter will be improved from about 0.011 inch to 0.005 inch in the mill annealed condition when heated at 1300 F.
- the variation in wire diameter is reduced from a starting figure of between 0.013 inch and 0.009 inch down to a maximum of 0.002 inch, and under the most rapid heating and cooling conditions, less even than this.
- the beta transes of the Ti-SSA commercially pure titanium metal was 1675 F. so that the beta heat-treatments used were all about above the beta transes temperature of the alloy. It will be seen from the variation in diameter of the cold drawn wire that the tests run using longer heating and cooling periods, that is 30 minutes to 1 hour, showed less favorable variation in wire diameter than the tests run at shorter periods of time.
- Table 2 following, provides examples of heat-treating alpha-beta type titanium base alloy above its beta transes temperature and subsequently cold drawing this through multiple edge-grooved rolls to produce wire of improved circularity.
- the wire was of an alloy comprising 8% aluminum, 1% molybdenum, 1% vanadium, and balance substantially all titanium.
- the original ingot of titanium base alloy was worked down through various stages, the wire being rolled on a hot mill starting at a temperature of about 1950 F. and finishing at a temperature of about 1400 F. to 1500 F. The latest prior working (at 1400 F. to 1500 F.) was in the alpha-beta field.
- Table 2 shows the heat-treatment prior to drawing through the edgegrooved rolls, the starting diameter of the wire, which was measured as maximum and minimum diameters along a 4-foot length of wire, and also the diameter measured in the same manner after drawing through the edgegrooved rolls.
- the variations in starting diameters and in the diameters after drawing through the edge-grooved rolls as well as the reduction in area and observations with respect to cracking during drawing are also shown in the table.
- Beta Transes 280-. 285 0. 005 245-. 247 0. 002 24 Do. 1,950 F. (10 Sec.) AC. 2 279-. 283 0. 004 245-. 246 0 001 24 D0. 281-. 283 0. 002 245-. 247 0 002 24 Do. 279-. 283 0. 004 244-. 246 0. 002 24 Do.
- the original ingot of the titanium base alloy was worked down through various stages, the wire being rolled on a hot mill starting at a temperature of about 1850 F. and finishing at a temperature of about 1300 F. to 1400 F.
- the latest prior working was in the alpha field.
- Table 3 shows the heat-treatment prior to drawing through the edge-grooved rolls, the starting diameter of the wire, which was measured as maximum and minimum diameters along a 4-foot length of wire, and also the diameter measured in the same manner after drawing through the edge-grooved rolls.
- the variations in starting diameters and in the diameters after drawing through the edge-grooved rolls as well as the reduction in area, and observations with respect to cracking during drawing, are also shown in the table.
- Table 3 following, provides examples of heat-treating an alpha type titanium base alloy above its beta transes It will be seen from Table 3 that with a heat-treatment below the beta transes with subsequent rapid cooling, the variation in wire diameter was improved in the case of the 5Al-2.5Sn titanium base alloy only from an average of 0.016 inch to an average of 0.007 inch. In addition, it will be seen that severe cracking occurred when sufiicient working was employed to provide a reduction in area during cold drawings through the edge-grooved rolls of 20%. When the reduction was reduced below 20%, cracking was avoided. The last result in the group of tests in which the alloy wire was heat-treated at 1850 F.
- the variation in starting diameter was reduced under these conditions into stages, that is from an original 0.016 inch down to 0.003 inch and then from 0.003 inch down to 0.002. inch in the second reduction. While the improvement in variation of diameter in the cold drawn wire in the second reduction stage is insignificant and also immaterial (since the starting diameter variation was already extremely low) a significant effect is seen in the amount of reduction which can be obtained without cracking in the product wire. It is shown under the test conditions that the wire can be reduced a total of 34% and still produce good wire without cracks. In the case of wire not heat-treated above its beta transes and shown as the bottom test of the upper group in Table 3, a combined reduction of 32% resulted in severe cracking in the wire product.
- a method for reducing the cross section of wire of metal selected from the group consisting of commercially 35 pure titanium and alpha-type and alpha-beta-type titanium base alloys, the latest prior working of said wire being hot-rolling below its beta transes temperature which comprises:
- a method for reducing the cross section of wire of metal selected from the group consisting of commercially pure titanium and alpha-type and alpha-beta-type titanium base alloys, the latest prior working of said wire being hot-rolling below its beta transes temperature which comprises:
- a method as set forth in claim 2 including passing electric current through said wire after said hot-rolling whereby said heating is accomplished by the resistance of 30 said wire to the passage of said electric current.
Description
y 3, 1968 w. M. PARRIS I ANNEALING TITANIUM WIRE Filed July 26, 1965 INVENTOR Warren M. Porris United States Patent 3,394,036 ANNEALENG TITANIUM WIRE Warren M. Parris, Las Vegas, Nev., assignor to Titanium Metals Corporation of America, New York, N.Y., a corporation of Delaware Filed July 26, 1965, Ser. No. 474,764 3 Claims. (Cl. 148-11.5)
ABSTRACT OF THE DISCLOSURE Method of reducing the cross section of titanium and titanium base alloy wire which has been previously hot rolled at a temperature below its beta transes comprising heating the wire to a temperature between the beta transes and about 100 F. above the beta transes followed by cooling to below the beta transes and cold drawing.
This invention relates to heat-treating wire and more particularly to annealing titanium or titanium base alloy wire to provide improved cold-rolling characteristics.
Conventional wire processing involves first hot-rolling to form a relatively large diameter wire which is subsequently cold drawn, often with several passes, through a die to provide the desired finished diameter. Instead of drawing through a die, the wire may be cold worked to finished diameter by passing through multiple circumferential rollers having grooved edges. Adjacent edges of the working rollers form a circular aperture so that the wire is worked down to provide the desired finished diameter by a rolling instead of a simple drawing operation.
A serious problem arises in production of such cold formed titanium and titanium alloy wire. Initial hot-rolling, most often accomplished at a temperature below the beta transes temperature and in the alpha-beta or alpha temperature field, produces a definite texture or preferred crystal orientation in the hot-rolled wire. When wire of this type of texture or orientation is subsequently coldrolled through a multiple roller finishing machine, the resistance of the wire to deformation is not uniform and the cross section of the cold-rolled wire will not be uniform and may actually be oval.
Summarized briefly, the process of this invention comprises heat-treating titanium and titanium alloy wire at a temperature above its beta transes to eliminate the crystal orientation imparted by previous hot-rolling at a temperature below its beta transes. This particular heating step, I have discovered, particularly in the case of titanium alloys, must be carried out so that the wire is heated rapidly to the heat-treating temperature, and then preferably cooled rapidly to prevent the, formation of large-size beta grain structure. When the wire is heattreated in this manner, being quickly raised to temperature and then quickly cooled, it can be reduced to final gauge through a roller type wire drawing machine to produce wire of circularity substantially improved over similar wire drawn without such heat-treatment, In addition, the ductility of the wire will be high so that its cross sectional area may be reduced by a substantial percentage in a single pass through the roller wheels without cracking or breaking of the wire.
The process of this invention may be more readily understood by reference to the single figure of the drawings in which a drum or coil of wire, which has previously been hot-rolled at a temperature below its beta transes, is shown at 2. The wire 4 is directed into resistance heating furnace 6 in which are arranged two sets of contact rollers indicated at 8 and 10 respectively, these two sets of rollers being spaced apart along the wire and each connected to a pole of a suitable source of electric current 12. The section of wire 4 between contact rollers 8 and 10 will complete the electrical circuit, and because of its own internal resistance, will be very rapidly raised to high temperature. Immediately on emergence from furnace 6 the wire is exposed to a blast of cooling air 14 provided by blower 16.
After cooling, the wire is pulled through a set of edgegrooved rolls 18, these in the illustration being a set of three arranged around the wire at a radial angle of each to the other with their edge grooves 20 forming a circular aperture through which the wire 4 is pulled by action of bull block 22 actuated by a suitable motor (not shown).
For simplicity and clarity and to illustrate the essential steps of the process, only one set of rolls 18 have been shown in the drawing. In practice, at least a pair of such sets, preferably nested to provide close coupling, will generally be employed so that the wire may be reduced in diameter in a plurality of steps. The first set of a pair may advantageously reduce the wire and give it a curved-side triangle cross section or oval or other non-circular shape, with the second and final set of rolls providing a circular aperture to impart the desired circular cross section.
The wire whose cross section is to be reduced by th method of this invention is characterized by having been previously worked at a temperature below its beta transes. It is common practice in wire manufacture to work commercially pure and alpha and alpha-beta type titanium base alloys in the alpha-beta field or alpha field because this provides easiest plastic deformation without raising the temperature of the material to a point where rapid oxidation and surface deterioration takes place. Moreover, working in the beta field will generally result in larger grains which are difiicult to break down in subsequent working at lower temperatures. The process of this invention is to be applied to wire whose latest prior working will have been hot-rolling at a temperature below its beta transes because this type of rolling apparently produces a detrimental crystal structure which affects subsequent cold-rolling when the wire is drawn through edge-grooved rolls. Apparently hot-rolling at such temperatures results in an orientation of the metal crystals so that subsequent deformation will not be uniform in all directions. Particularly when the hot-rolled Wire is drawn through edge-grooved rolls the ease of deformation in a plane perpendicular to the length of the wire will not be uniform at various radial angles in this plane. Consequently, such wire when cold drawn through edgegrooved rolls will deform more readily in certain areas or directions, and this will often result in an oval wire instead of having desired circular cross section. It appears that the edge-grooved rolls, no matter how strongly built and precisely aligned to produce a circular orifice through which the wire is drawn, can be deformed elastically to some extent so that wire having preferred crystal orientation, when passing through such rolls, will not produce a truly circular or uniform reduced cross section wire.
According to this invention, however, heating the wire to above its beta transes and subsequently cooling the wire with attention to rapid heating and cooling, for the titanium base alloys particularly, results: in an annealed wire of uniform crystal orientation which, when cold drawn through edge-grooved rolls, can be reduced to produce a circular 'wire of substantially uniform diameter.
The wire should be heated to a temperature definitely above its beta transes temperature, which may be determined for commercially pure titanium or any of the alpha or alpha-beta type titanium base alloys by metallurgical methods well known in the art. The minimum time that the wire is maintained above its beta transes temperature is not critical, since apparently transformation takes place almost instantaneously; and once the wire has been raised to above its beta transes and subsequently cooled, the time above the beta transes temperature, even though but a few seconds, will be sufiicient to produce the desired transformation of the crystal structure. It is preferred to heat the wire to a temperature between its beta transes and 100 F. above its beta transes in order to be sure that all portions of the wire have definitely been raised to above the beta transes temperature. Preferably the heat treating temperature is between the beta transes temperature and about 50 F. above the beta transes. While the temperature should be sufficiently higher than the beta transes to insure complete transformation, it is not desirable to raise to excessive temperature since this inevitably results in increased time above the beta transes, and also results in a tendency towards formation of large beta grains.
The time for the heat-treating step of this invention is extremely critical, and for alpha and alpha-beta type titanium base alloys the total elapsed time for heating the wire from room temperature to above its beta transes plus the time it is maintained above its beta transes should not be greater than one minute. Preferably for best results with wire of the recited titanium base alloys the time should not be more than 30 seconds. For comcient that the temperature be rapidly reduced, and to accomplish this, air cooling will produce a relatively fast and efficient reduction of wire temperature from its annealed temperature down to room temperature and particularly at least through the beta transes temperature.
After heat-treatment and subsequent cooling, the wire is cold drawn through a set of edge-grooved rolls to produce circular wire of substantially uniform diameter. Table 1, following, provides examples of heat-treating commercially pure titanium wire above its beta transes temperature and subsequently cold drawing this through two sets of nested edge grooved rolls to produce wire of improved circularity. The wire was of commercially pure, unalloyed titanium designated in the trade as Ti-SSA. The original ingot of the commercially pure titanium was worked down through various stages, the wire being rolled on a hot mill starting at a temperature of about ]750 F. and finishing at a temperature of about 1300 F. The latest prior working (at 1300 F.) was in the alpha field. Table 1 shows the heat-treatment prior to drawing through the edge-grooved rolls, the starting diameter of the wire, which was measured as maximum and minimum diameters along a 10-foot length of wire, and also the diameter measured in the same manner after cold drawing through the edgegrooved rolls.
TABLE 1 Variation in Starting Variation in DiameterAfter Diameter of Heat-Treatment Prior to Drawing Diameter Starting Drawing 1 Cold Drawn (inch) Diameter (inch) (inch) Wire (inch) As Mill Annealed 266-. 277 0. 011 .246-. 251 0. 005 1,300 F. (2 Hrs.) AC 2 71-. 280 0. 009 .246. 257 0, 011 Heat-Treated Above Beta Transes:
1,750 F. (10 See.) A 1641274 0.010 .2465.248 0.0015 750 F. (10 Sec AC 2 267-. 276 0. 000 2465-. 248 0.0015 1,750 F (15 Min.) AC 2 258-. 271 0. 013 246-. 247 0. 001 1,750 F. Min. AC .259. 272 0. 013 .246. 248 0.002 1,750" F (1 B AC 265-. 275 0.010 .246. 248 0.002
1 Maximum and minimum diameters along 10-fo 0t length of wire. 2 Total time heating to temperature and air cooling.
mercially pure titanium, the time is not so critical. I have found some improvement with shorter times, but wire of commercially pure titanium may be heat-treated through a cycle from room temperature to above the beta transes plus the time at or above the beta transes, which takes no more than one hour.
The short time requirements for the heat-treating step of this invention requires means for heating wire very rapidly to high temperature. This can readily be accomplished by resistance heating or induction heating. In resistance heating, heavy electrical currents are passed through a limited section of the wire, and the current flow results in extremely rapid heating of the wire. It is no problem to raise the wire temperature to above its beta transes temperature in a matter of seconds when passing a sufficient amount of current. In induction heating, the wire is subjected to high frequency induced electric current, and this also will raise the temperature of the wire extremely rapidly; and raising to above the beta transes by induction heating can be accomplished well within the time limits hereinbefore recited. When heattreating commercially pure titanium wire, and for which the time is not so critical, coils of wire may be furnace heat-treated, which takes appreciably longer than the other two methods suggested, but total heat-treating time may still be maintained within a desirable period under an hour.
Once the heat-treated wire has been raised to above its beta transes temperature, it is then quickly cooled, at least down through its beta transes. This may be accomplished by any convenient means providing a relatively rapid cooling. Quenching, which involves submerging the hot wire in water or oil and results in an almost instantaneous cooling, can be employed, if desired, although such a fast cooling effect is not essential to satisfactory results according to this invention. It is sufii- It will be seen from Table 1 that with a heat-treatment below the beta transes with subsequent rapid cooling, the variation in wire diameter will be improved from about 0.011 inch to 0.005 inch in the mill annealed condition when heated at 1300 F. When heat-treatment above the beta transes is employed, however, the variation in wire diameter is reduced from a starting figure of between 0.013 inch and 0.009 inch down to a maximum of 0.002 inch, and under the most rapid heating and cooling conditions, less even than this. The beta transes of the Ti-SSA commercially pure titanium metal was 1675 F. so that the beta heat-treatments used were all about above the beta transes temperature of the alloy. It will be seen from the variation in diameter of the cold drawn wire that the tests run using longer heating and cooling periods, that is 30 minutes to 1 hour, showed less favorable variation in wire diameter than the tests run at shorter periods of time.
Table 2, following, provides examples of heat-treating alpha-beta type titanium base alloy above its beta transes temperature and subsequently cold drawing this through multiple edge-grooved rolls to produce wire of improved circularity. The wire was of an alloy comprising 8% aluminum, 1% molybdenum, 1% vanadium, and balance substantially all titanium. The original ingot of titanium base alloy was worked down through various stages, the wire being rolled on a hot mill starting at a temperature of about 1950 F. and finishing at a temperature of about 1400 F. to 1500 F. The latest prior working (at 1400 F. to 1500 F.) was in the alpha-beta field. Table 2 shows the heat-treatment prior to drawing through the edgegrooved rolls, the starting diameter of the wire, which was measured as maximum and minimum diameters along a 4-foot length of wire, and also the diameter measured in the same manner after drawing through the edgegrooved rolls. The variations in starting diameters and in the diameters after drawing through the edge-grooved rolls as well as the reduction in area and observations with respect to cracking during drawing are also shown in the table.
TABLE 2.-8Al-1Mo-1V ALLOY Starting Variation in Diameter Variation in Reduction Diameter Starting After Draw- Diameter of in Area, Remarks (inch) Diameter, ing (inch) Cold Drawn Percent (inch) Wire, (inch) Heat-Treatment Prior to Drawing: 276-. 279 0. 003 243-. 249 0.006 21. 5 Severe Cracking.
1,850 F. (5 min.) AC 2 (cts Anneal). .279-. 282 0. 004 .254. 260 0. s 15. OK, No Cracks.
. 276-. 280 0. 004 252-. 256 0. 004 16. 5 Do. 276-. 278 0. 002 252-. 256 0. 004 16. 0 Do.
Average 0. 0035 0. 005
Heat-Treated Above Beta Transes: 280-. 285 0. 005 245-. 247 0. 002 24 Do. 1,950 F. (10 Sec.) AC. 2 279-. 283 0. 004 245-. 246 0 001 24 D0. 281-. 283 0. 002 245-. 247 0 002 24 Do. 279-. 283 0. 004 244-. 246 0. 002 24 Do.
Average 0. 004 0. 002
1 Maximum and minimum diameters along 4-foot length of wire. 2 Total time heating to temperature and air cooling.
It will be seen from Table 2 that with a heat-treatment below the beta transes and followed by subsequent rapid cooling, the variation in wire diameter will not be improved in the case of the 8Al-1Mo-1V alloy. The test results indicate that after a heat-treatment at 185 0 F. the variation in starting diameter averaged 0.0035 inch; and this was made worse by cold drawing, the average after this step being 0.005 inch. It will also be seen from the results shown in the upper portion of Table 2 that cold drawing to produce a reduction in area of as much as 21.5% resulted in severe cracking of the product wire, although reductions in the range of 15.5% to 16.5% could be obtained with no cracks. When the 8Al-1Mo-1V wire was heat-treated at a temperature above its beta transes, that is at 1950 F. (its beta transes being 1900 F.), and
The original ingot of the titanium base alloy was worked down through various stages, the wire being rolled on a hot mill starting at a temperature of about 1850 F. and finishing at a temperature of about 1300 F. to 1400 F. The latest prior working (at 1300" F. to 1400 F.) was in the alpha field. Table 3 shows the heat-treatment prior to drawing through the edge-grooved rolls, the starting diameter of the wire, which was measured as maximum and minimum diameters along a 4-foot length of wire, and also the diameter measured in the same manner after drawing through the edge-grooved rolls. The variations in starting diameters and in the diameters after drawing through the edge-grooved rolls as well as the reduction in area, and observations with respect to cracking during drawing, are also shown in the table.
TABLE 3.5A1-2.5S11 ALLOY Starting Variation in Diameter Variation in Reduction Diameter, 1 Starting After Draw- Diameter of in Area, Remarks (inch) Diameter, ing, 1 (inch) Cold Drawn Percent (inch) Wire (inch) Heat-Treatment Prior to Drawing: 287-. 305 0.018 261-. 268 0. 007 20 Severe Cracking. 1,850 F. (5 Min.) AC 2 (a-fi Anneal). 287-. 306 0.019 267-. 273 0.006 16. 5 OK, No Cracks.
. 288-. 308 0. 020 264-. 273 0. 009 19 Do. 290-. 306 0. 016 264-. 273 0. 009 19 Do. 286-. 306 0. 020 264-. 271 0. 007 18 D0. 3 264-. 271 0. 007 3 242-. 247 0. 005 32 Severe Cracking.
Average 0. 016 0. 007
Heat-Treated Above Beta Transes: .293-. 311 0. 018 261-. 264 0.003 24. 5 OK, No Cracks.
1,950 F. (10 Sec.) AC 2 291-. 307 0. 016 262-. 264 0. 002 22. 5 Do. 289-. 303 0. 014 260-. 263 0.003 22. 0 Do. 290-. 306 0. 016 260. 263 0. 003 22. 0 D0.
Average 0. 016 0.003
a .261-. 264 0. 003 3 244-. 24s 0. 002 n 34 Do. 5 260-. 263 0.003 3 244-. 246 0. 002 34 D0. 3 260-. 263 0. 003 3 244-. 246 0. 002 34 Do. 3 .262-. 264 0. 002 3 .244. 246 0. 002 34 Do.
Average 0. 003 0. 002
1 Maximum and minimum diameters along 4-foot length of wire.
2 Total time heating to temperature and air cooling.
3 Second reduction without intermediate anneal.
rapidly cooled by air cooling, the variation in diameter before and after drawing through the edge-grooved rolls was reduced from an average of 0.004 inch to an average of 0.002 inch. Thus it is seen that the critical heat-treating and rapid cooling resulted in a substantial improved circularity and uniformity of diameter of the cold drawn wire. Additionally, it will be noted that after heat-treating according to this invention and cold drawing through the edge-grooved rolls, a reduction in area of 24% could be readily obtained without cracking of the wire product, and this compares with substantially less reduction obtainable without the specific he-at-treatment employed according to this invention and shown in the upper part of the table.
Table 3, following, provides examples of heat-treating an alpha type titanium base alloy above its beta transes It will be seen from Table 3 that with a heat-treatment below the beta transes with subsequent rapid cooling, the variation in wire diameter was improved in the case of the 5Al-2.5Sn titanium base alloy only from an average of 0.016 inch to an average of 0.007 inch. In addition, it will be seen that severe cracking occurred when sufiicient working was employed to provide a reduction in area during cold drawings through the edge-grooved rolls of 20%. When the reduction was reduced below 20%, cracking was avoided. The last result in the group of tests in which the alloy wire was heat-treated at 1850 F. prior to cold drawing through the edge-grooved rolls was given a second reduction without intermediate anneal so that the total reduction amounted to 32%. Apparently the alloy wire was not sufficiently ductile to maintain its integrity 7 under this degree of reduction and severe cracking resulted.
In the group of tests which were heat-treated above the beta transes of the alloy, namely at 1950 F. and then rapidly reduced in temperature by air cooling, the average variation in starting diameter was reduced from 0.016 inch down to 0.003 inch. The beta transes of the Al-2.5Sn alloy is 1900 F. In the upper group of tests in which the wire had been heat-treated above its beta transes, it will be seen that reduction in area of as high as 24.5% could be obtained without any deleterious effect on the wire, that is without formation of cracks. In the lower group of tests in Table 3, also heat-treated at 1950 F. and rapidly reduced in temperature by air cooling, the wire was given a second reduction without intermediate anneal to provide a total reduction in area of 34%. The variation in starting diameter was reduced under these conditions into stages, that is from an original 0.016 inch down to 0.003 inch and then from 0.003 inch down to 0.002. inch in the second reduction. While the improvement in variation of diameter in the cold drawn wire in the second reduction stage is insignificant and also immaterial (since the starting diameter variation was already extremely low) a significant effect is seen in the amount of reduction which can be obtained without cracking in the product wire. It is shown under the test conditions that the wire can be reduced a total of 34% and still produce good wire without cracks. In the case of wire not heat-treated above its beta transes and shown as the bottom test of the upper group in Table 3, a combined reduction of 32% resulted in severe cracking in the wire product.
I claim:
1. A method for reducing the cross section of wire of metal selected from the group consisting of commercially 35 pure titanium and alpha-type and alpha-beta-type titanium base alloys, the latest prior working of said wire being hot-rolling below its beta transes temperature, which comprises:
(a) heating said wire to a temperature between its beta transes temperature and about 50 F. above its beta transes temperature and subsequently cooling said wire to below its beta transes temperature, the total elapsed time for heating said wire from room temperature to above its beta transes temperature plus the time it is maintained above its beta transes temperature being not greater than one minute; and,
5 (b) cold drawing said wire through edge-grooved rolls, whose edge grooves in adjacent alignment form a circular aperture to provide a circular wire of substantially uniform diameter.
2. A method for reducing the cross section of wire of metal selected from the group consisting of commercially pure titanium and alpha-type and alpha-beta-type titanium base alloys, the latest prior working of said wire being hot-rolling below its beta transes temperature, which comprises:
(a) heating said wire to a temperature between its beta transes temperature and about 100 F. above its beta transes temperature and subsequently cooling said wire to below its beta transes temperature, the total elapsed time for heating said wire from room temperature to above its beta transes temperature plus the time it is maintained above its beta transes temperature being not greater than one minute; and,
(b) cold drawing said wire through edge-grooved rolls whose edge grooves in adjacent alignment form a circular aperture to provide a circular wire of substantially uniform diameter.
3. A method as set forth in claim 2 including passing electric current through said wire after said hot-rolling whereby said heating is accomplished by the resistance of 30 said wire to the passage of said electric current.
References Cited UNITED STATES PATENTS 2,804,409 8/1957 Kessler et al. 1481l.5 3,169,085 2/1965 Newman 1481l.5
FOREIGN PATENTS 949,861 2/1964 Great Britain.
HYLAND BIZOT, Primary Examiner.
W. W. STALLARD, Assistant Examiner.
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US474764A US3394036A (en) | 1965-07-26 | 1965-07-26 | Annealing titanium wire |
GB33109/66A GB1104500A (en) | 1965-07-26 | 1966-07-22 | A method of reducing the cross-section of titanium or titanium-base alloy wire |
DE19661533486 DE1533486A1 (en) | 1965-07-26 | 1966-07-22 | Process for reducing the cross section of wire made of titanium or titanium alloys |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
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US474764A US3394036A (en) | 1965-07-26 | 1965-07-26 | Annealing titanium wire |
Publications (1)
Publication Number | Publication Date |
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US3394036A true US3394036A (en) | 1968-07-23 |
Family
ID=23884841
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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US474764A Expired - Lifetime US3394036A (en) | 1965-07-26 | 1965-07-26 | Annealing titanium wire |
Country Status (3)
Country | Link |
---|---|
US (1) | US3394036A (en) |
DE (1) | DE1533486A1 (en) |
GB (1) | GB1104500A (en) |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3470034A (en) * | 1967-02-14 | 1969-09-30 | Reactive Metals Inc | Method of refining the macrostructure of titanium alloys |
US3481799A (en) * | 1966-07-19 | 1969-12-02 | Titanium Metals Corp | Processing titanium and titanium alloy products |
US3492172A (en) * | 1966-11-09 | 1970-01-27 | Titanium Metals Corp | Method for producing titanium strip |
US3511622A (en) * | 1965-10-12 | 1970-05-12 | Milton A Nation | Titanium wire and wire rope |
US3527044A (en) * | 1968-05-20 | 1970-09-08 | Milton A Nation | Inertial concept for cable dynamics |
US3532559A (en) * | 1967-09-11 | 1970-10-06 | Int Nickel Co | Cold reduced titanium-base alloy |
US3645123A (en) * | 1966-02-18 | 1972-02-29 | Andre Auge | Process for making metallic wires and metallic wires prepared thereby |
US4224085A (en) * | 1978-07-21 | 1980-09-23 | The International Nickel Co., Inc. | Wire forming process |
US4494307A (en) * | 1982-01-08 | 1985-01-22 | Les Cables De Lyon | Method of manufacturing electric cable having compressed mineral insulation and a titanium sheath |
US5256216A (en) * | 1991-02-22 | 1993-10-26 | Compagnie Europeenne Du Zirconium Cezus | Controlled resistive heat treatment for a continuously moving zircaloy sheet |
WO1995010983A1 (en) * | 1993-10-20 | 1995-04-27 | Florida Hospital Supply | Process of manufacturing an aneurysm clip |
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CN113600616B (en) * | 2021-08-09 | 2023-05-30 | 成都先进金属材料产业技术研究院股份有限公司 | Thermal processing method for improving high-speed impact resistance of two-phase titanium alloy |
CN114769339B (en) * | 2022-05-03 | 2022-09-30 | 兴化市顺杰高温合金制品有限公司 | Cold drawing machine for cold working extension of high-temperature alloy wire |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2804409A (en) * | 1956-02-06 | 1957-08-27 | Titanium Metals Corp | Heat treating titanium-base alloy products |
GB949861A (en) * | 1961-02-07 | 1964-02-19 | Crucible Steel International S | Improvements in production of titanium and titanium-base alloys |
US3169085A (en) * | 1963-02-20 | 1965-02-09 | Jeremy R Newman | Method of producing titanium base strip |
-
1965
- 1965-07-26 US US474764A patent/US3394036A/en not_active Expired - Lifetime
-
1966
- 1966-07-22 DE DE19661533486 patent/DE1533486A1/en active Pending
- 1966-07-22 GB GB33109/66A patent/GB1104500A/en not_active Expired
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2804409A (en) * | 1956-02-06 | 1957-08-27 | Titanium Metals Corp | Heat treating titanium-base alloy products |
GB949861A (en) * | 1961-02-07 | 1964-02-19 | Crucible Steel International S | Improvements in production of titanium and titanium-base alloys |
US3169085A (en) * | 1963-02-20 | 1965-02-09 | Jeremy R Newman | Method of producing titanium base strip |
Cited By (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3511622A (en) * | 1965-10-12 | 1970-05-12 | Milton A Nation | Titanium wire and wire rope |
US3645123A (en) * | 1966-02-18 | 1972-02-29 | Andre Auge | Process for making metallic wires and metallic wires prepared thereby |
US3481799A (en) * | 1966-07-19 | 1969-12-02 | Titanium Metals Corp | Processing titanium and titanium alloy products |
US3492172A (en) * | 1966-11-09 | 1970-01-27 | Titanium Metals Corp | Method for producing titanium strip |
US3470034A (en) * | 1967-02-14 | 1969-09-30 | Reactive Metals Inc | Method of refining the macrostructure of titanium alloys |
US3532559A (en) * | 1967-09-11 | 1970-10-06 | Int Nickel Co | Cold reduced titanium-base alloy |
US3527044A (en) * | 1968-05-20 | 1970-09-08 | Milton A Nation | Inertial concept for cable dynamics |
US4224085A (en) * | 1978-07-21 | 1980-09-23 | The International Nickel Co., Inc. | Wire forming process |
US4494307A (en) * | 1982-01-08 | 1985-01-22 | Les Cables De Lyon | Method of manufacturing electric cable having compressed mineral insulation and a titanium sheath |
US5256216A (en) * | 1991-02-22 | 1993-10-26 | Compagnie Europeenne Du Zirconium Cezus | Controlled resistive heat treatment for a continuously moving zircaloy sheet |
WO1995010983A1 (en) * | 1993-10-20 | 1995-04-27 | Florida Hospital Supply | Process of manufacturing an aneurysm clip |
US5758420A (en) * | 1993-10-20 | 1998-06-02 | Florida Hospital Supplies, Inc. | Process of manufacturing an aneurysm clip |
Also Published As
Publication number | Publication date |
---|---|
DE1533486A1 (en) | 1970-04-02 |
GB1104500A (en) | 1968-02-28 |
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