US3099592A - Process of annealing low carbon steel - Google Patents

Process of annealing low carbon steel Download PDF

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US3099592A
US3099592A US1774A US177460A US3099592A US 3099592 A US3099592 A US 3099592A US 1774 A US1774 A US 1774A US 177460 A US177460 A US 177460A US 3099592 A US3099592 A US 3099592A
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temperature
annealing
steel
softening
low carbon
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Garber Sidney
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British Iron and Steel Research Association BISRA
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing

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  • This invention relates to processes of annealing low carbon steels and particularly to processes of annealing such steels after cold working by heating to a subcritical annealing temperature and subsequently cooling.
  • the material is first heated to 670 C., this temperature being reached after 25 seconds in the heating zone of the furnace. The material remains at this temperature in a soaking zone for 10 /2 seconds, after which it is cooled. Cooling takes place in three stages: a slow cool lasting seconds from 670 C. to 425 C., a fast cool lasting 81 /2 seconds from 425 C. to 115 C., and a forced air cool lasting 11 seconds from 115 to 60 (3.; this time-temperature cycle is shown by a dashed line in the single FIGURE of the accompanying drawing in which temperature (in C.) is plotted against time (in seconds). With reference to such a time-temperature cycle, it has now been found that:
  • the relatively slow controlled cooling has been thought to be necessary to avoid the hardening effects that occur when low carbon steels are rapidly cooled or quenched from temperatures above 300 C.; on the other hand, the metal must remain inside the furnace for an excessively long time so that the speed of the throughput is limited by the length of the furnace which is already very long, and if a breakage occurs with this excessive length of blackplate or strip within the furnace 2 to 16 hours are required to rethread the furnace.
  • a process of annealing cold worked low carbon steel which comprises the steps of rapidly quenching the steel from a subcritical annealing temperature and thereafter carrying out an age softening treatment.
  • the two operations of quenching and age softening can be carried out separately, that is by quenching to room temperature and subsequently carrying out the age softening treatment, or they can be combined by quenching the steel to the age softening temperature and holding it at this tempertaure until softening occurs.
  • the latter is, however, to be preferred from both a practical viewpoint, that is it does not necessitate re-heating of the steel to the softening temperature, and from a metallurgical viewpoint, in that the most consistent results are obtained and quench ageing does not occur.
  • Such quenching and age softening is capable of giving a product whose quality is at least as good as that produced in known continuous systems employing large furnaces, while the cost of the age softening equipment is relatively much smaller and there is considerable saving in space.
  • the quenching and age softening may be carried out as soon as the effects of work hardening have been removed by recovery or recovery and recrystallisation after the comparatively slow heating and soaking periods of a known annealing cycle. It is preferred, however, to effect quenching and age softening after rapid heating of the steel to the subcritical annealing temperature, i.e. recrystallisation temperature, as this gives rise to a large grain size and enables the soaking period of the known annealing cycle to be eliminated thus making possible a further increase in. the speed of a continuous or semicontinuous annealing line, or alternatively a reduction in the size of the furnace.
  • rapid heating of the steel to the recrystallisation temperature involves heating in less than half the time required in the known annealing cycle. It is, in fact, preferred to effect heating to this temperature in from 1 to 10 seconds.
  • a fairly wide range of temperatures are suitable for the age softening treatment and the temperature chosen will depend upon the degree of softening it is desired to attain as the higher the temperature the greater the degree of softening. It has been found that 200 C. is about the minimum temperature at which age softening can be carried out and suitable temperatures are from 200 C. to about 450 "C. At temperatures from 200 C. to about 250 C., age softening may be effected in air as substantially no oxidation of the steel occurs at these temperatures; above 250 "C. age softening should be carried out in a non-oxidising atmosphere as the amount of oxidation which would occur in air at these temperatures would be sufiicient to interfere with subsequent operations, such as tinning.
  • the minimum time of holding at the softening temperature in order to obtain a product with stable mechanical properties depends on the softening temperature; at lower temperatures longer holding times are required than at higher softening temperatures. Thus at 200 C., a holding time of 30 to 50 minutes is required, while at about 300 C., from 15 to 30 minutes is required. Within these limits of holding time, the degree of softening can be varied by choice of holding time, the shorter the holding time, the smaller being the degree of softening.
  • the age softening treatment is conveniently carried out by coiling the steel as soon as it reaches the desired softening temperature; due to its bulk and shape in coil form, the steel in most cases cools slowly enough to allow sutficient time for complete age softening to occur. If a longer holding time is required, the rate of cooling of the coiled material may be retarded by extraneous means.
  • a typical annealing cycle according to the present invention is illustrated, by way of example only, by the full line curve in the accompanying drawing.
  • This annealing cycle was applied to the continuous treatment of cold worked blackplate having a thickness of 0.014 inch moving at 500 feet per minute.
  • the blackplate was first heated to 700 C. in 5 seconds and then immediately quenched to 300 C. in 5 seconds and was then immediately coiled at the latter temperature, the coiler being located in a nonoxidising atmosphere.
  • the coil of black plate' was allowed to cool slowly in the non-oxidising atmosphere for from to minutes.
  • a slow cool from the recrystallisation temperature i.e. about 700 C.
  • 600 C. taking from 3 to 4 seconds can be effected before quenching.
  • This slow cool makes it easier to obtain the desired degree of softening with the lower age softening temperatures, for example from 200 to 250 C., and is therefore advantageous in enabling the age softening treatment to be carried out without a nonoxidising atmosphere, and thus with simpler plant.
  • the capital costs of a continuous annealing furnace for low carbon steels, together with the difliculties attendant upon the threading of long lengths of steel through a furnace, may be reduced to a marked extent by use of the present invention.
  • the invention is not restricted to continuous annealing; for example, it can be adapted to semi-continuous and batch annealing of heavily cold worked low carbon steel.
  • a process for the continuous high speed annealing of cold-reduced low carbon steel strip suitable for the production of tinplate comprises the steps of rapidly heating the steel to a subcritical annealing temperature of about 700 C., whereby recrystallisation of the steel is effected, quenching the steel from the annealing temperature in not more than 5 seconds to a temperature of from 200 to 250 C., coiling the strip at the latter temperature and maintaining the coiled strip within said temperature range for from 30 to minutes.
  • a process for the continuous high speed annealing of cold-reduced low carbon steel strip suitable for the production of tinpiate comprises the steps of rapidly heating the steel to a subcritical annealing temperature of about 700 C., whereby recrystallisation of the steel is effected, quenching the steel from the annealing temperature in not more than 5 seconds to a temperature of from 250 C. to 450 C., coiling the strip at the latter temperature, and maintaining the coiled strip in a non-0xidising atmosphere within said temperature range for from 15 to 30 minutes.
  • a process according to claim 4 in which the steel is heated up to the subcritical annealing temperature in from 1 to 10 seconds and said rapid quenching is carried out immediately the steel reaches said temperature.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Description

July 30, 1963 s, GARBER 3,099,592
PROCESS OF ANNEALING LOW CARBON STEEL Filed Jan. 11, 1960 I I I I I I I I I l l l "a I 5 8 I, U) l I- I I f I I o o o o 0 o o o o 0 o 0 o o h o m q m N s aanivaadwai i I INVENTOR I arm/v5 r G/FRBER ATTORNEY:
3,099,592 PROCESS OF ANNEALING LGW CARBON STEEL Sidney Gar-her, Sheffield, England, assignor to The British Iron and Steel Research Association Filed Jan. 11, 1960, Ser. No. 1,774 6 Claims. (Cl. 143-144) This invention relates to processes of annealing low carbon steels and particularly to processes of annealing such steels after cold working by heating to a subcritical annealing temperature and subsequently cooling.
In the continuous annealing of low carbon steel strip in modern strip and tinplate mills, the annealing cycle imposes a limit upon the linear speeds of the annealing lines, and the attainment of the speeds at present in use has only been made possible by the utilisation of large and extremely costly furnaces and equipment. Between one-half and one mile of strip may be enclosed in such an annealing furnace together with the inlet and exit loopers. In addition, the extremely fine grain of the continuous annealed product limits the range of uses to which it can be put; continuously annealed blackplate, for example, may be employed only for products normally made from tempers 4, and 6, and thicker sheet and strip are similarly restricted in their uses.
It is an object of the invention to provide a process of annealing low carbon steel, applicable to the continuous annealing of steel strip or blackplate, which makes it possible to maintain existing speeds in continuous annealing with smaller and simpler furnaces, or alternatively to increase existing throughput speeds with the furnaces of the sizes at present in use. It is a further object of the invention to provide a process of annealing which is capable of providing a metallurgically improved quality of continuous annealed sheet or blackplate.
In one known time-temperature annealing cycle used in continuous annealing treatment, the material is first heated to 670 C., this temperature being reached after 25 seconds in the heating zone of the furnace. The material remains at this temperature in a soaking zone for 10 /2 seconds, after which it is cooled. Cooling takes place in three stages: a slow cool lasting seconds from 670 C. to 425 C., a fast cool lasting 81 /2 seconds from 425 C. to 115 C., and a forced air cool lasting 11 seconds from 115 to 60 (3.; this time-temperature cycle is shown by a dashed line in the single FIGURE of the accompanying drawing in which temperature (in C.) is plotted against time (in seconds). With reference to such a time-temperature cycle, it has now been found that:
(1) By heating up cold-reduced, low carbon steel to the subcritical annealing temperature, which is at or about 700 C., rapidly, that is in less than half the heating time required in the known annealing cycle, the ultimate grain size after recrystallisation appears to be larger than when the material is heated up at the relatively slower rate of the known cycle.
(2) Further, since the heavily cold worked material recrystallises almost instantaneously when the subcritical annealing temperature is reached, holding the metal at annealing temperatures for any period up to 10 minutes does not appreciably increase the grain size. Hence, the soaking period of the known annealing cycle is superfluous.
(3) The major time portion of the known time-temperature cycle is taken up by cooling. For example, 92 /2 seconds out of a total cycle time of 143 seconds are taken up by cooling from 425 C. to 60 C. Metallurgically, this part of the cycle has a relatively minor role in the annealing process since it actually plays no part in the recrystallisation which is the major softening mechnit ttes tnti ice anism. The relatively slow controlled cooling has been thought to be necessary to avoid the hardening effects that occur when low carbon steels are rapidly cooled or quenched from temperatures above 300 C.; on the other hand, the metal must remain inside the furnace for an excessively long time so that the speed of the throughput is limited by the length of the furnace which is already very long, and if a breakage occurs with this excessive length of blackplate or strip within the furnace 2 to 16 hours are required to rethread the furnace.
It has now been found that the time required for the cooling portion of the annealing cycle can be radically reduced by rapidly quenching the steel after recrystallisation and removing any increased hardness due to quenching by an age softening treatment.
According to the present invention, therefore, there is provided a process of annealing cold worked low carbon steel which comprises the steps of rapidly quenching the steel from a subcritical annealing temperature and thereafter carrying out an age softening treatment.
The two operations of quenching and age softening can be carried out separately, that is by quenching to room temperature and subsequently carrying out the age softening treatment, or they can be combined by quenching the steel to the age softening temperature and holding it at this tempertaure until softening occurs. The latter is, however, to be preferred from both a practical viewpoint, that is it does not necessitate re-heating of the steel to the softening temperature, and from a metallurgical viewpoint, in that the most consistent results are obtained and quench ageing does not occur.
Such quenching and age softening is capable of giving a product whose quality is at least as good as that produced in known continuous systems employing large furnaces, while the cost of the age softening equipment is relatively much smaller and there is considerable saving in space.
The quenching and age softening may be carried out as soon as the effects of work hardening have been removed by recovery or recovery and recrystallisation after the comparatively slow heating and soaking periods of a known annealing cycle. It is preferred, however, to effect quenching and age softening after rapid heating of the steel to the subcritical annealing temperature, i.e. recrystallisation temperature, as this gives rise to a large grain size and enables the soaking period of the known annealing cycle to be eliminated thus making possible a further increase in. the speed of a continuous or semicontinuous annealing line, or alternatively a reduction in the size of the furnace. As stated above, rapid heating of the steel to the recrystallisation temperature involves heating in less than half the time required in the known annealing cycle. It is, in fact, preferred to effect heating to this temperature in from 1 to 10 seconds.
A fairly wide range of temperatures are suitable for the age softening treatment and the temperature chosen will depend upon the degree of softening it is desired to attain as the higher the temperature the greater the degree of softening. It has been found that 200 C. is about the minimum temperature at which age softening can be carried out and suitable temperatures are from 200 C. to about 450 "C. At temperatures from 200 C. to about 250 C., age softening may be effected in air as substantially no oxidation of the steel occurs at these temperatures; above 250 "C. age softening should be carried out in a non-oxidising atmosphere as the amount of oxidation which would occur in air at these temperatures would be sufiicient to interfere with subsequent operations, such as tinning. The minimum time of holding at the softening temperature in order to obtain a product with stable mechanical properties depends on the softening temperature; at lower temperatures longer holding times are required than at higher softening temperatures. Thus at 200 C., a holding time of 30 to 50 minutes is required, while at about 300 C., from 15 to 30 minutes is required. Within these limits of holding time, the degree of softening can be varied by choice of holding time, the shorter the holding time, the smaller being the degree of softening.
The age softening treatment is conveniently carried out by coiling the steel as soon as it reaches the desired softening temperature; due to its bulk and shape in coil form, the steel in most cases cools slowly enough to allow sutficient time for complete age softening to occur. If a longer holding time is required, the rate of cooling of the coiled material may be retarded by extraneous means.
A typical annealing cycle according to the present invention is illustrated, by way of example only, by the full line curve in the accompanying drawing. This annealing cycle was applied to the continuous treatment of cold worked blackplate having a thickness of 0.014 inch moving at 500 feet per minute. The blackplate was first heated to 700 C. in 5 seconds and then immediately quenched to 300 C. in 5 seconds and was then immediately coiled at the latter temperature, the coiler being located in a nonoxidising atmosphere. The coil of black plate'was allowed to cool slowly in the non-oxidising atmosphere for from to minutes. At the end of this time, its Vickers hardness was 105-115 D.P.N., while the Vickers hardness of the same blackplate which had been annealed by the known annealing cycle shown by the dashed curve in the accompanying drawing was 115 D.P.N.
Instead of quenching the steel immediately it reaches the recrystallisation temperature, a slow cool from the recrystallisation temperature (i.e. about 700 C.) to about 600 C. taking from 3 to 4 seconds, can be effected before quenching. This slow cool makes it easier to obtain the desired degree of softening with the lower age softening temperatures, for example from 200 to 250 C., and is therefore advantageous in enabling the age softening treatment to be carried out without a nonoxidising atmosphere, and thus with simpler plant.
The capital costs of a continuous annealing furnace for low carbon steels, together with the difliculties attendant upon the threading of long lengths of steel through a furnace, may be reduced to a marked extent by use of the present invention. At the same time, the invention is not restricted to continuous annealing; for example, it can be adapted to semi-continuous and batch annealing of heavily cold worked low carbon steel.
What I :claim is:
1. A process for the continuous high speed annealing of cold-reduced low carbon steel strip suitable for the production of tinplate, which process comprises the steps of rapidly heating the steel to a subcritical annealing temperature of about 700 C., whereby recrystallisation of the steel is effected, quenching the steel from the annealing temperature in not more than 5 seconds to a temperature of from 200 to 250 C., coiling the strip at the latter temperature and maintaining the coiled strip within said temperature range for from 30 to minutes.
2. A process according to claim 1, in which the steel is heated up to the subcritical annealing temperature in from 1 to 10 seconds and said rapid quenching is carried out immediately the steel reaches said temperature.
3. A process according to claim 1, in which the steel is cooled from the subcritical annealing temperature to about 600 C. in from 3 to 4 seconds prior to said rapid quenching.
4. A process for the continuous high speed annealing of cold-reduced low carbon steel strip suitable for the production of tinpiate, which process comprises the steps of rapidly heating the steel to a subcritical annealing temperature of about 700 C., whereby recrystallisation of the steel is effected, quenching the steel from the annealing temperature in not more than 5 seconds to a temperature of from 250 C. to 450 C., coiling the strip at the latter temperature, and maintaining the coiled strip in a non-0xidising atmosphere within said temperature range for from 15 to 30 minutes.
5. A process according to claim 4, in which the steel is heated up to the subcritical annealing temperature in from 1 to 10 seconds and said rapid quenching is carried out immediately the steel reaches said temperature.
6. A process according to claim 4, in which the steel is cooled from the subcritical annealing temperature to about 600 C. in from 3 to 4 seconds prior to said rapid quenching.
References Cited in the file of this patent UNITED STATES PATENTS 2,095,580 Whetzel Oct. 12, 1937 2,283,109 Von Ende May 12, 1942 2,393,363 Gold et al Jan. 22, 1946 2,405,946 Gat et al Aug. 20, 1946 2,597,979 Darmara May 27, 1952 2,634,964 "Cooper Apr. 14, 1953 2,872,173 Munker Feb. 3, 1959 OTHER REFERENCES Ricketet al.: Transactions of the ASM, volume 41, 1949, pages 1113-1141.
Metals Handbook. Published by the ASM, 1948 Edition, page 631.
The Making, Shaping and Treating of Steel by U.S.S., 7th Edition, 1957.

Claims (1)

1. A PROCESS FOR THE CONTINUOUS HIGH SPEED ANNELING OF COLD-REDUCED LOW CARBON STEEL STRIP SUITABLE FOR THE PRODUCTION OF TINPLATE, WHICH PROCESS COMPRISES THE STEPS OF RAPIDLY HEATING THE STEEL TO A SUBCRITICAL ANNEALING TEMPERATURE OF ABOUT 700*C., WHEREBY RECRYSTALLISATION OF THE STEEL IS EFFECTED, QUENCHING THE STEEL FROM THE ANNEALING TEMPERATURE IN NOT MORE THAN 5 SECONDS TO A TEMPERATURE OF FROM 200* TO 250*C., COILING THE STRIP AT THE LATTER TEMPERATUURE AND MAINTAINING THE COILED STRIP WITHIN SAID TEMPERATURE RANGE FOR FROM 30 TO 50 MINUTES.
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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3160533A (en) * 1960-03-08 1964-12-08 Rasselstein Ag Heat treatment for the production of a low carbon steel sutable for deformation without cutting
US4323403A (en) * 1972-06-22 1982-04-06 Nippon Kokan Kabushiki Kaisha Continuous annealing method for cold reduced steel strip
WO2000039349A1 (en) * 1998-12-28 2000-07-06 Robert Bosch Gmbh Method for hardening and tempering steel strips
EP1088902A1 (en) * 1999-09-30 2001-04-04 Thyssen Krupp Stahl AG Process for manufacturing aging-resistant aluminium killed steel strip
WO2001027340A1 (en) * 1999-10-13 2001-04-19 Centre De Recherches Metallurgiques Method for making a cold rolled steel strip for deep-drawing

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2095580A (en) * 1934-06-01 1937-10-12 American Sheet & Tin Plate Steel strip and its production
US2283109A (en) * 1940-02-26 1942-05-12 Ende Herman L Von Bluing steel
US2393363A (en) * 1943-03-15 1946-01-22 Nat Steel Corp Heat treatment of thin metal articles
US2405946A (en) * 1943-01-06 1946-08-20 Carnegie Illinois Steel Corp Production of non-aging steel
US2597979A (en) * 1949-12-21 1952-05-27 United States Steel Corp Recrystallizing deep-drawing steel
US2634964A (en) * 1951-01-09 1953-04-14 Cold Metal Products Company Conveyer furnace
US2872173A (en) * 1949-12-12 1959-02-03 Munker Theo Method and apparatus for heat treating materials in a continuous operating furance

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2095580A (en) * 1934-06-01 1937-10-12 American Sheet & Tin Plate Steel strip and its production
US2283109A (en) * 1940-02-26 1942-05-12 Ende Herman L Von Bluing steel
US2405946A (en) * 1943-01-06 1946-08-20 Carnegie Illinois Steel Corp Production of non-aging steel
US2393363A (en) * 1943-03-15 1946-01-22 Nat Steel Corp Heat treatment of thin metal articles
US2872173A (en) * 1949-12-12 1959-02-03 Munker Theo Method and apparatus for heat treating materials in a continuous operating furance
US2597979A (en) * 1949-12-21 1952-05-27 United States Steel Corp Recrystallizing deep-drawing steel
US2634964A (en) * 1951-01-09 1953-04-14 Cold Metal Products Company Conveyer furnace

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3160533A (en) * 1960-03-08 1964-12-08 Rasselstein Ag Heat treatment for the production of a low carbon steel sutable for deformation without cutting
US4323403A (en) * 1972-06-22 1982-04-06 Nippon Kokan Kabushiki Kaisha Continuous annealing method for cold reduced steel strip
WO2000039349A1 (en) * 1998-12-28 2000-07-06 Robert Bosch Gmbh Method for hardening and tempering steel strips
EP1088902A1 (en) * 1999-09-30 2001-04-04 Thyssen Krupp Stahl AG Process for manufacturing aging-resistant aluminium killed steel strip
WO2001027340A1 (en) * 1999-10-13 2001-04-19 Centre De Recherches Metallurgiques Method for making a cold rolled steel strip for deep-drawing
BE1012934A3 (en) * 1999-10-13 2001-06-05 Ct Rech Metallurgiques Asbl Manufacturing method of steel strip for cold rolled deep.
US6638380B1 (en) 1999-10-13 2003-10-28 Centre De Recherches Metallurgiques Method for making a cold rolled steel strip for deep-drawing

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