US3239388A - Cold rolled rimmed steel sheet and strip having preferred orientation adapted for press forming and production of the same - Google Patents

Cold rolled rimmed steel sheet and strip having preferred orientation adapted for press forming and production of the same Download PDF

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US3239388A
US3239388A US286994A US28699463A US3239388A US 3239388 A US3239388 A US 3239388A US 286994 A US286994 A US 286994A US 28699463 A US28699463 A US 28699463A US 3239388 A US3239388 A US 3239388A
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steel sheet
steel
strip
cold rolled
rimmed
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Sasaki Kenji
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JFE Steel Corp
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Kawasaki Steel Corp
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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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0457—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/08—Extraction of nitrogen
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing

Definitions

  • an aluminum stabilized steel has been widely employed as a deep drawing steel sheet and strip.
  • the aluminum stabilized steel sheet or strip is produced by the steps of making a steel ingot which has been deoxidized to a high degree by aluminum in an ingot casting step followed by a hot rolling step and a cold rolling one, and annealing a steel sheet or strip to precipitate aluminum nitride, whereby an elongated grain structure is formed in it.
  • the aluminum stabilized steel sheet or strip has a superior deep drawing property, it has heretofore been attributed to the fact that the elongated grain structure has caused the deformation resistance in a thickness direction to be greater than the deformation resistance in a plane so that the thinning in thickness has been reduced.
  • the steel sheet or strip provided with the above quality in accordance with this invention has been accomplished by the process comprising the steps of adding one or more of the elements selected from the group consisting of antimony, bismuth and niobium into a molten steel produced by the open hearth furnace, the electric furnace and the converter in either a steel making or ingot casting step to obtain rimmed steel ingots containing one or more of said elements singly or combined in a total amount of 0.003-0.100% by weight, then subjecting said steel to hot and cold rolling, then annealing the cold rolled rimmed steel sheet or strip at a temperature of 500750 C. in an atmosphere containing hydrogen and moisture to decarburize its carbon content less than 0.020% or decarburize and denitride its carbon content less than 0.020% and its nitrogen content less than 0.002%.
  • the decarburizing annealing step and the decarburizing and denitriding annealing one described in the present invention are achieved by subjecting the cold rolled rimmed steel sheet or strip to an anneal in an atmosphere containing hydrogen and moisture at the temperature of 500-750 C. for a predetermined period of time.
  • the period of time required for the anneal depends upon the steel sheet thickness and the composition of the atmosphere.
  • the velocity of decarburization is relatively so fast that carbon is removed sufiiciently at an early period of the anneal, but, on the other hand, the velocity of denitridation is so low even in an atmosphere, such as AX gas, containing a low nitrogen content that it will take a pretty long period of time until a desired low nitrogen content is attained in the steel sheet.
  • an atmosphere such as AX gas
  • denitridation is hardly efiected even in the atmosphere containing a high nitrogen content.
  • an annealing step in the atmosphere consisting of a major part of N and a minor part of H and H 0, such as DX gas with appropriate moisture, for a relatively short period with a view to decarburizing only is relied upon to produce a cold rolled rimmed steel sheet or strip having a better drawability than that of the commercial one of prior art.
  • a preferred embodiment of this invention comprises making steel by the known basic open hearth furnace, adding bismuth to the thus obtained molten steel, and producing a rimmed steel ingot containing 0.060% carbon and 0.015% bismuth.
  • a cold rolled strip coil of 0.8 mm. in thickness is produced by the known process of slabbing, hot rolling and cold rolling.
  • this strip coil is subjected to a decarburizing annealing in an open coil annealing furnace at about 700 C. for a period of 40 hours in DX atmosphere with moisture, and to known skin pass rolling, which results in the production of excellent deep drawing cold rolled steel sheet and having the following properties: R 1.65, Er. 11.20 mm., C.C.V. 35.70 mm., TS. 293 kg./mm. and El. 50%
  • the chemical analysis and mechanical properties of the present steel sheet are listed as No. 6 data in Table 1.
  • One of the features of this invention is to provide the formation of the preferred orientation favorable to the deep drawing process by the steps of adding a minor amount of one or more of antimony, bismuth and niobium to the steel and subjecting the thus produced steel to heat treatment.
  • the steel sheet or strip of this invention can be produced from a relatively low cost rimmed steel, therefore it is less expensive than the aluminum stabilized steel or strip.
  • the steel sheet or strip of this invention is superior to any other steel sheet or strip in the deep drawing property.
  • Table 1 shows the plastic strain ratio (1?), the conical cup value (C.C.V.), various mechanical properties and the intensity of (111) plane difiraction peak by the X-ray inverse pole figure method, all
  • FIG. 1 A circular blank is rested horizontally in the conical die, and drawn with the appropriate punchuntil the bottom of the cup fractures.
  • Table 3 The dimensional specifications are given in Table 3.
  • the die hole diameters specified are such that no ironing of the cup occurs as it enters the die hole. Blanks should be cleaned and then lubricated and. the speed of drawing is virtually immaterial.
  • FIG. 1 shows a sectional view of the arrangement of tools for the conical cup test.
  • FIG. 2 shows a perspective view of a shape of fractured cup as the result of test.
  • FIG. 3. shows a perspective view of another shape of fractured cup.
  • FIG. 4 shows a perspective view of a shape of a completely drawn cupwith no fracture.
  • the conical cup value (C.C.V.) is represented by the numerical value, mm., of the average diameter of the rim of the conical cup when fracture occurs as shown in FIGS; 2'3.
  • the conical cup value shown in FIG. 3, which is less than that of FIG. 2, is obtained from the steel sheet having a better deep drawability than that of the one shown in FIG. 2.
  • the shape of the completely drawn cup with no fracture shown in FIG. 4 is attained by the steel sheet of a very high deep drawability, and in this case, no value of conical cup test is obtained, but represented as drawn through in Table 1.
  • C.C.V. of various. steel sheet listed in Table 1 are the measurements conducted on the sheet of the thickness, 0.8 mm. by means of the die type 17 of Table 3.
  • Table 4 the minimum standard value for showing the drawability of each sheet of a particular thickness produced by the process of this invention is listed.
  • the sheet of .I IS this invention 13 26.40 or less 13 26.40 or less 17 37.30 or less 17 37.42 or less 21 44.82 or less 21 45.12 or less log W /W
  • W width of tensile test specimen before tension
  • E value the lessthinning in the thickness direction in the plastic deformation, and the more the deformation in the width direction.
  • the crystallo-' graphic orientation of the rimmed steel sheet of this invention containing a small amount. of antimony, bismuth v and niobium is different from that-of the knownrirnmedsteel sheet which has been decarburized and denitrided.
  • the Xray itensity of (111.) plane difiraction peak of the known rimmed steel is small while that of the steel sheet produced from the known rimmed steel which has been subjected to thedecarburizing and denitriding annealing is also relatively small.
  • the accumulation of the main crystallographic. orientation (111) plane of the present decarburizcd and idenitrided rimmed steel sheet containing antimony, bismuth and nio-. bium is stronger.
  • the intensityof (111) planeydiftraction peak of the aluminum stabilized steel isstronger than-that of the known rimmed steel, but weaker than that of :the present steel sheet.
  • Table 2 shows the results of various practical press forming tests conducted on various steel sheet. In each press forming. test shown'inrTable 2, the stretch formability refers to theileft' side while the: deep drawability to the right more emphatically than the other,'respectively.
  • the decarburized and denitrided rimmed steel sheet or strip containing antimony, bismuth and niobium of the present invention has not only the excellent deep drawing property but also the good stretch formability. It will be appreciated, therefore, that this steel sheet or strip is well suited for all type of press forming.
  • the aging velocity of the present steel sheet is considerably slower than that of the commercial rimmed steel sheet of prior art, and if the carbon and nitrogen content can be reduced by the decarlburizing and denitriding annealing, the present steel will be given the non-aging property.
  • the steel sheet or strip of the invention will have an adequate nonaging quality if the elements, carbon, nitrogen, antimony, bismuth and niobium are contained in the steel in the above-mentioned range.
  • a method for producing cold rolled rimmed steel sheet and strip having good drawability and stretchability comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.0030.100% by weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing anneal to decrease its carbon content to less than 0.020% by weight.
  • a thickness selected from the range of 0.5 to 1.6 mm. comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.003-0.100% by Weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing anneal to decrease its carbon content to less than 0.020% by weight.
  • a method for producing cold rolled rimmed steel sheet and strip having good drawability and stretchability comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.003-0.100% by weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing and denitriding anneal to decrease its carbon content to less than 0.020% and its nitrogen content to less than 0.002%.
  • a thickness selected from the range of 0.5 to 1.6 mm. comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.003 0.100% by weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing and denitriding anneal to decrease its carbon content to less than 0.020% and its nitrogen content to less than 0.002%.
  • a cold rolled decarburized rimmed steel sheet or strip having good drawability and stretchability said steel consisting essentially of at least one element selected from the group consisting of antimony, bismuth and niobium, the total element percentage being 0.0030.100% by weight, less than 0.020% carbon, OAS-0.60% manganese, and the balance iron and incidental impurities.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
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Description

March 8, 1966 KENJI s s K 3,239,388
OOLD ROLLED RIMMED sTEEL SHEET AND STRIP HAVING PREFERRED ORIENTATION ADAPTED FOR PRESS FORMING AND PRODUCTION OF THE SAME Filed June 11, 1963 ZZZ; 1
$15 Z FIE 5 LWJ LIA (mm) (mm) United States Patent 3,239,388 COLD ROLLED RIMMED STEEL SHEET AND STRIP HAVING PREFERRED ORIENTATION ADAPT- ED FOR PRESS FORMING AND PRODUCTION OF THE SAME Kenji Sasaki, Inagedai-machi, Chiba-shi, Japan, assignor to Kawasaki Steel Corporation, Kobe-shi, Japan, a corporation of Japan Filed June 11, 1963, Ser. No. 286,994 Claims priority, application Japan, July 11, 1962, 37/29,166 18 Claims. (Cl. 148-2) The present invention relates to the cold rolled rimmed steel sheet and strip having a preferred orientation adapted for press forming and the production of the same.
Heretofore an aluminum stabilized steel has been widely employed as a deep drawing steel sheet and strip. The aluminum stabilized steel sheet or strip is produced by the steps of making a steel ingot which has been deoxidized to a high degree by aluminum in an ingot casting step followed by a hot rolling step and a cold rolling one, and annealing a steel sheet or strip to precipitate aluminum nitride, whereby an elongated grain structure is formed in it. In reference to the reason why the aluminum stabilized steel sheet or strip has a superior deep drawing property, it has heretofore been attributed to the fact that the elongated grain structure has caused the deformation resistance in a thickness direction to be greater than the deformation resistance in a plane so that the thinning in thickness has been reduced.
However, after an extensive study of the aluminum stabilized steel sheet or strip by means of the X-ray diffraction method, it has been found that the excellent deep drawing property of the aluminum stabilized steel sheet or strip is not attributed to the form of grains, but to the preferred orientation caused by the conditions of the steel sheet or strip making process.
Having our attention focused on the conditions of the steel sheet or strip production advantageous for the formation of the preferred orientation favorable to the deep drawing quality together with the effect of addition of minor elements, I, inventor, have completed the present invention.
The steel sheet or strip provided with the above quality in accordance with this invention has been accomplished by the process comprising the steps of adding one or more of the elements selected from the group consisting of antimony, bismuth and niobium into a molten steel produced by the open hearth furnace, the electric furnace and the converter in either a steel making or ingot casting step to obtain rimmed steel ingots containing one or more of said elements singly or combined in a total amount of 0.003-0.100% by weight, then subjecting said steel to hot and cold rolling, then annealing the cold rolled rimmed steel sheet or strip at a temperature of 500750 C. in an atmosphere containing hydrogen and moisture to decarburize its carbon content less than 0.020% or decarburize and denitride its carbon content less than 0.020% and its nitrogen content less than 0.002%.
The decarburizing annealing step and the decarburizing and denitriding annealing one described in the present invention are achieved by subjecting the cold rolled rimmed steel sheet or strip to an anneal in an atmosphere containing hydrogen and moisture at the temperature of 500-750 C. for a predetermined period of time. The period of time required for the anneal depends upon the steel sheet thickness and the composition of the atmosphere. In reference to the behavior of carbon and nitrogen in the annealing process, the velocity of decarburization is relatively so fast that carbon is removed sufiiciently at an early period of the anneal, but, on the other hand, the velocity of denitridation is so low even in an atmosphere, such as AX gas, containing a low nitrogen content that it will take a pretty long period of time until a desired low nitrogen content is attained in the steel sheet. However, denitridation is hardly efiected even in the atmosphere containing a high nitrogen content.
In order to obtain the steel sheet or strip having a good drawability as well as non-aging property, it is effective to decrease the carbon and nitrogen contents thereof as low as possible by subjecting it to annealing in the atmosphere consisting of a major part of H and a minor part of N and H 0.
From an economical point of view for the purpose of attaining a low cost production of a steel sheet having a good drawability with an inferior non-aging property, an annealing step in the atmosphere consisting of a major part of N and a minor part of H and H 0, such as DX gas with appropriate moisture, for a relatively short period with a view to decarburizing only is relied upon to produce a cold rolled rimmed steel sheet or strip having a better drawability than that of the commercial one of prior art.
A preferred embodiment of this invention comprises making steel by the known basic open hearth furnace, adding bismuth to the thus obtained molten steel, and producing a rimmed steel ingot containing 0.060% carbon and 0.015% bismuth.
Then, a cold rolled strip coil of 0.8 mm. in thickness is produced by the known process of slabbing, hot rolling and cold rolling.
Subsequently, this strip coil is subjected to a decarburizing annealing in an open coil annealing furnace at about 700 C. for a period of 40 hours in DX atmosphere with moisture, and to known skin pass rolling, which results in the production of excellent deep drawing cold rolled steel sheet and having the following properties: R 1.65, Er. 11.20 mm., C.C.V. 35.70 mm., TS. 293 kg./mm. and El. 50%
The chemical analysis and mechanical properties of the present steel sheet are listed as No. 23 data in Table 1.
Another preferred embodiment of this invention comprises making steel by the known basic open hearth furnace, adding antimony to the thus obtained molten steel, and producing a rimmed steel ingot containing 0.08% carbon and 0.025% antimony. Then, a cold rolled strip coil of 0.8 mm. in thickness is produced by the known process of slabbing, hot rolling and cold rolling. Subsequently, this strip coil is subjected to a decarburizing and denitriding annealing in an open coil annealing furnace at about 700 C. for a period of 40 hours in AX atmosphere with moisture, and to known skin pass rolling, which results in the production of excellent deep drawing cold rolled steel sheet and having the following properties: E 1.82, Er. 11.13, C.C.V. drawnthrough, T.S. 29.0 kg./m=m. and El. 48%. The chemical analysis and mechanical properties of the present steel sheet are listed as No. 6 data in Table 1.
One of the features of this invention is to provide the formation of the preferred orientation favorable to the deep drawing process by the steps of adding a minor amount of one or more of antimony, bismuth and niobium to the steel and subjecting the thus produced steel to heat treatment. The steel sheet or strip of this invention can be produced from a relatively low cost rimmed steel, therefore it is less expensive than the aluminum stabilized steel or strip. Moreover, the steel sheet or strip of this invention is superior to any other steel sheet or strip in the deep drawing property. The excellent prop- 3 erties of the steel sheet or strip of this invention will now be described hereinbelow in the following description. Table 1 shows the plastic strain ratio (1?), the conical cup value (C.C.V.), various mechanical properties and the intensity of (111) plane difiraction peak by the X-ray inverse pole figure method, all
of which have been deter- I mined onthe commercial rimmed steel, the aluminum taining various: amounts of antimony, bismuth and .nio-' 5 biurn.
TABLE 1 Chemical Analysis (Percent) Specimen steel 0' S1 Mn P Com rim. ste Tr. 0. 32 O. 010 Com. rim. steel de-C deN anneal Tr. 0. 33 0.010 Al stabilized steel- Tr. 0. 30 0. 008 Sb-cont. de-C. de-N. rim. steel 0. 004 Tr. 0.32 0. 010 (in 0.006 Tr. 0.32 0.010 do 0.006 Tr. 0. 32, 0. 010 0. 005 Tr. 0. 32 0. 010 rln O. 006 Tr. 0. 32 0.010 Bi cont. de-C. de-N. rim. steel 0.007 Tr. 0.33 0.011 0. 006 Tr. 0.32 0.010 (in i 0.007 Tr. 0. 32 0. 100 Nb cont. 'de-C. de-N. rim. steel 0.007 Tr. 0.33 0.011 (in 0.004 Tr. 0.33 0. 010 jn 0. 005 Tr. 0. 32 0. 010 dn 0. 009 Tr. 0. 32 0. 011 Sb-Bi cont. de-C. tie-N. rim. steel. 0. 009 Tr. 0. 34 0. 015 -dn 0. 007 Tr. 0. 36 0. 014 Sb-N b cont. (10 C. de-N. rim. steel 0. 008 Tr. 0. 38 0. 013 dn 0. 008 Tr. 0.37 0. 013 Bi-Nb cont. de-C. de-N. rim. steel 0.008 Tr. 0.34 0.014 dn 0. 007 Tr. 0.35 0. 013 Sb cont. de-C. rim. steel 0. 008 Tr. 0. 34 0.012 Bi cont. de-C. rim. steel 0.009 Tr. 0.33 0.010 Nb cont. de-O. rim. steel 0.009 Tr. 0.34 0.010
Chemical Analysis (percent) Specimen N o.
S Al Sb Bi Nb N 0. 013 Tr. Tr. Tr." Tr. 0. 0025 0. 014 T1. Tr. Tr. Tr. 0. 0008 0. 010 0. 060 Tr. Tr. Tr. 0.0058 0. 013 Tr. 0. 005 Tr. Tr. 0. 0007 0. 013 Tr. 0.013 Tr. Tr. 0. 0009 0. 013 Tr. 0. 025 T1. Tr. 0. 0009 0. 013 Tr. 0. 050 Tr! Tr. 0. 0008 0.013 Tr. O. 084 Tr. Tr. 0. 0010 0. 014 T1. T1. 0. 005 Tr; 0. 0008 0. 013 Tr; Tr. 0. 011' Tr. 0.0009 0. 013 Tr. Tr. 0. 030 Tr. 0. 0008 0. 014 Tr. Tr. Tr. 0. 005 0. 0008 0. 012, T1. Tr; Tr. 0. 013 0. 0009 0. 013 Tr. Tr. Tr. 0. 028 0. 0008 0. 013 T1. Tr. Tr. 0. 048 0. 0010 0. 018 Tr. 0. 005 0. 005' Tr. 0. 0013 0. 017 Ti. 0. 018 0. 013 T1. 0. 0012 0. 017 TI. 0. 005 T1. 0. 005 0. 0009 0. 016 Tr. 0. 010 T1. 0. 019 0. 0008 0. 018 Tr. Tr. 0. 005 0. 005 0. 0009 0. 017 Tr. Tr. 0. 012 0. 015 0.0010 0. 012 Tr. 0. 024 Tr. Tr. 0.0024 0. 013 Tr. Tr. 0. 015 Tr. 0. 0021 0. 013 Tr. Tr. Tr. 0. 014 0. 0023 Mechanical Properties Intensity of (111) a plane dif- C.C.V., EL, Er., T.S., Y.P., Y.E.,' fraction R mm percent mm. kg./. kg./ percent peak.
mm. mm.
1. 07 38. 45 10. 20 32. 8 3.0 3. 5 1. 40 37. 51 10; 84 28. 3 0. 5 8. 0 1. 55 37. 47 10; 30. 5 0. 0 9. 0 1. 36.80 51 12.11 28. 4 0.2 10.5 1. 78 35. 73 49 11. 28. 5 0. 2 l4. 0 1. 82 48 11. 13 29. 0. 0. 0 14. 5 1. 80 47 10; 55 31. 3 0. 0 14. 4 1. 75 35. 97 45 10. 40 34. 0 0. 0 13.8 1. 52 37. 19 51 11. 90 28. 2 0. 2 9. 2 1. 72 35. 41 50 11. 35 28.5 0.2 10. 6 1.81 48 10. 91 29. 4 0. 2 l1. 0 1. 57 37. 37 52 11. 43 28. 0 0. 0 9. 8 1. 68 26. 50 52 11. 67 28. 8 0. 0 10. 9 1. 78 52 11. 54 28.4 0. 0 12. 9 1. 75 35.02 51 11.02 29.3 0.0 11.0 1. 74 36. 5O 49 11. 20 28. 5 0. 5 9. 6 1. 80 35. 80 48 10. 52 29. 0 0. 2 10. 5 1. 36.53 50 11. 00 28.6 0. 0 9.8 1. 71 36.48 48 10. 28. 8 0. 0 10. 4 1. 58 36. 51 11. 05 28. 2 0. 0 9. 4 1. 75 35.75 50 10.95 28.5 0. 0 11.0 1. 76 35. 47 10.90 29. 2 18. 5 1. 2 12. 8 1. 65 35. 70 50 11. 20 29. 3 17. 5 1.0 10.2 1. 70 36. 30 50 11. 50 29. 0 17.0 0. 7 11. 01
1 Drawn through.
TABLE 2 Chemical Analysis (Percent) Steel Si Mn P S Al Sb Bi Com. rim. steel 0.055 Tr. 0.35 0. 010 0.014. Tr. Tr. Tr. Al stabilized steel- 0. 045 Tr. 0. 3O 0. 008 0. 010 0. 055 Tr. Tr. De-C. de-N. rim. steel 0.006 Tr. 0.34 0. 012 0.014 Tr. Tr. Tr. Sb-eont. de-G. (le-N. rim. steel- 0.004 Tr. 0.33 0. 010 I 0.014 Tr 0. 023 Tr. Bi-cont. de-O. de-N. rim. steel--- 0. 006 Tr. 0.34 0. 012 0.010 Tr. Tr 0.012 Nb-cont. de-C. de-N. rim. steel 0.007 Tr. 0. 0. 010 0. 014 Tr. Tr. Tr.
Punch Shape Chemical Analysis. Round Round Round Round Flat Flat (percent) Blank dia., mm.
Steel Blank Holder Pressure (ton) 1 Nb N Measurement Stretch Stretch Stretch Flange Flange Flange Depth, Depth, 7 Depth, Strain Strain Strain mm. mm. 2. mm. ratio, a ratio, a ratio, a I percent percent percent Com. rim. steel T T1. 0. 0022- 44. 5 50.0 01. 5 4. 78 3. 93 9. Al stabilized steel- Tr. 0.0058 45.0 50. 5 66. 0 7. 78 5. 94 18.89- De-C. de-N. rim. steel- Tr. 0. 0008 46. 5 51. 0 65. 5 7. 5. 62 14. 52 Sb-cont. de-G. de-N. rim. steel Tr. 0.0008' 46. 5 51.0 68.0 8. 91 6. 59 Bi-cont. deC. de-N. rim. steel Tr. 0. 0009 46.7 51. 5 67. 5 8. 52 6. 28 25. 41 Nb-cont. de-O. de-N. rim. steel 0.010 0.0008 47.0 51. 5 68.0 9.12 5. 69 14. 60
1 Drawn through. N orn.100-,tou press test. Die and Punch in detail.
Punch shape:
(a) Round: Hemisphere. (b), Flat: Profile radius. 10B. Punch diameter- 100 mm. 5. Die diameter- 102.4 mm. qS. Die profile radius 5R. Blank holder diameter 300 mm.
The Japanese Industrial Standard. Z-2249, relating to the method. of conical cup test, has been recently published. In this conical cup test, it is possible to draw a steel sheet without forming wrinkles and without applying; any blankholder pressure provided the correct blank diameter is selected with respect only to sheet thickness. The effect of bending and unbending, which is an important factor in a cylindrical cup-forming test, is also less important in the conical cup. test. A hemispherically ended punch with a profile radius of approximately 5 to 10' times the thickness of the test blank is used. The rating of drawability is obtained from the average diameter of the rim of the conical cup when fracture occurs. Since the blank diameter is fixed only by the sheet thickness, the test is simple and quick.
The principle of'the test is illustrated. in FIG. 1. A circular blank is rested horizontally in the conical die, and drawn with the appropriate punchuntil the bottom of the cup fractures. The dimensional specifications are given in Table 3.
The die hole diameters specified are such that no ironing of the cup occurs as it enters the die hole. Blanks should be cleaned and then lubricated and. the speed of drawing is virtually immaterial.
The conical cup-forming test of the Japanese Industrial Standard, X-2249, is performed in an arrangement of tools for a conical cup test shown in the accompanyin g drawing, in which:
FIG. 1 shows a sectional view of the arrangement of tools for the conical cup test.
FIG. 2 shows a perspective view of a shape of fractured cup as the result of test.
FIG. 3. shows a perspective view of another shape of fractured cup.
FIG. 4 shows a perspective view of a shape of a completely drawn cupwith no fracture. More particularly, the conical cup value (C.C.V.) is represented by the numerical value, mm., of the average diameter of the rim of the conical cup when fracture occurs as shown in FIGS; 2'3. The conical cup value shown in FIG. 3, which is less than that of FIG. 2, is obtained from the steel sheet having a better deep drawability than that of the one shown in FIG. 2. The shape of the completely drawn cup with no fracture shown in FIG. 4 is attained by the steel sheet of a very high deep drawability, and in this case, no value of conical cup test is obtained, but represented as drawn through in Table 1.
In order to obtain the conical cup value or C.C.V. of a steel sheet of a particular thickness, the particular tools specified. by JIS Z-2249 as shown in Table 3 should be employed. C.C.V. of various. steel sheet listed in Table 1 are the measurements conducted on the sheet of the thickness, 0.8 mm. by means of the die type 17 of Table 3. In Table 4, the minimum standard value for showing the drawability of each sheet of a particular thickness produced by the process of this invention is listed.
TABLE 3 Blank thickness, mm.
Over 0.5 Over 0.8 Over 1.0 Over 1.3
. .0, to 1.3, excl. excl. excl. incl.
Die Type 13 17 21 27 Blank 'dia., 410, mm 36 78 Conical half-angle of die, 8- 60 60 60 60 Die hole dia., dz, mm 14. 60 19. 95 24. 40- 32.0 Die profile radius r mm 3.0 4.0 6.0 8.0 Ball radius, 1,, mm (i 41 (1 d Iuneh dia. :1 mm 12. 17. 46 20. 64 26. 99
TABLE 4 C.C.V. of Sheet Thickness Die Type, the sheet of .I IS this invention 13 26.40 or less 13 26.40 or less 17 37.30 or less 17 37.42 or less 21 44.82 or less 21 45.12 or less log W /W where W =width of tensile test specimen before tension W-=width of tensile test specimen after tension t =thickness of tensile test specimen before tension t thickness of tensile test specimen after tension The greater the E value the lessthinning in the thickness direction in the plastic deformation, and the more the deformation in the width direction.
It follows that the steel sheet material having a large R value is excellent in the deep drawing property, since the fracture in the deep drawing process is caused by the necking due to the decrease of sheet thickness. As matter of fact, in obtaining the I? value, it is difficult to conduct an accurate determination of the thinning in the thickness direction. So we measured the elongation of gauge length of the tensile test specimen by means of the electronic strain meter and the mean width of the specimen. The Ti value obtained from the following formula, provided that the volume of the deformed test specimen being constant:
1 gauge length before tension. l= gauge length after tension.
E 10g l0g l-wll -w By the above measurement, the test errors are very small. For this test specimen, a tensile test specimen (gauge length 50 mm.) of HS (Japanese Industrial Standard) No. 5 is employed, and the Rvalue in 15% extension is obtained. In general, as the .R value depends on the direction from which the test specimen is taken, the measurement along the three directions, rolling direction (R 45 .degrees to the rolling direction, (R and 90 degrees to the rolling direction (R is made, and the 8% mean value E is obtained from the; following formula: (Rt) (Ra +202) As clearly shown in the Ti value and the X-ray intensity of. (111) plane diffraction peak of Table? 1, the crystallo-' graphic orientation of the rimmed steel sheet of this invention containing a small amount. of antimony, bismuth v and niobium is different from that-of the knownrirnmedsteel sheet which has been decarburized and denitrided. Thus, the Xray itensity of (111.) plane difiraction peak of the known rimmed steel is small while that of the steel sheet produced from the known rimmed steel which has been subjected to thedecarburizing and denitriding annealing is also relatively small. Compared ,to the above, the accumulation of the main crystallographic. orientation (111) plane of the present decarburizcd and idenitrided rimmed steel sheet containing antimony, bismuth and nio-. bium is stronger.
The intensityof (111) planeydiftraction peak of the aluminum stabilized steel isstronger than-that of the known rimmed steel, but weaker than that of :the present steel sheet.
value of the, commercial rimmedsteelis the least of all, that of the decar-burized and. denitrided rimmed steel larger, and that of thealuminum stabilized steel the largest. The fi value of the present decarburized and denitrided rimmed steel sheet containing antimony, bismuth and niobium .is also equal to or larger than that of the.
aluminum stabilized 'steel.
In case (111) plane is parallel with thelrolling surface,
the fact that the: i value is made? large can be explained theoretically as follows: when the-slip direction is only [111] direction. while deformation, and when (111) plane As described hereinabovepa favorable v effect'of antimony, bismuth and niobium, on the deep drawingqualitv of the steel sheet is apparent. However, in the practical press forming process, the formation of miscellaneous complicated shapes is required [so much ithat not only the high degree deep drawability but also the high stretch formability should .be given to the steel sheet. ence to the characteristic value for showing stretch formability, both elongation, EL and the -Erichsen value,--Er. are universally adopted.
As clearly illustratedin ,Tablei 1,?the. steel sheet containing a suitable amount of antimony, bismuth and niobium has a good conical cup value as well as good El. and
Er. values, and the sheetcontaining niobium has asuperior stretch formability.
Table 2.shows the results of various practical press forming tests conducted on various steel sheet. In each press forming. test shown'inrTable 2, the stretch formability refers to theileft' side while the: deep drawability to the right more emphatically than the other,'respectively.
In the press forming requirements, the greater the blank holder pressure, the larger. the blank diameter; and .the round punch rather than the flat one will all favor the stretch formability more emphatically in the press forming .test. Three measurements in. the left refer. tothe depth, mm., of penetration when fractureoccurs. Three values in the right'refer 'to the flange strain ratio'oc:
The above-mentionedrelationship is" made i more distinct in the R valueof Table 1.1 Thus, the F In referwhere D =blank diameter before press forming D =mean diameter after press forming As is evident from Table 2, the deep drawing property of the commercial rimmed steel sheet is considerably inferior to that of other steel sheet for the same purpose, but the stretch formability thereof is relatively good. The aluminum stabilized steel sheet shows the mean values both in the deep drawability and stretch formability.
Compared to the above, the decarburized and denitrided rimmed steel sheet or strip containing antimony, bismuth and niobium of the present invention has not only the excellent deep drawing property but also the good stretch formability. It will be appreciated, therefore, that this steel sheet or strip is well suited for all type of press forming.
As to the aging property of the present steel sheet, the aging velocity thereof is considerably slower than that of the commercial rimmed steel sheet of prior art, and if the carbon and nitrogen content can be reduced by the decarlburizing and denitriding annealing, the present steel will be given the non-aging property. However, from an industrial and economical point of view, it will be adequate if no stretcher-strains occur in press forming. The steel sheet or strip of the invention will have an adequate nonaging quality if the elements, carbon, nitrogen, antimony, bismuth and niobium are contained in the steel in the above-mentioned range.
I claim:
1. A method for producing cold rolled rimmed steel sheet and strip having good drawability and stretchability comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.0030.100% by weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing anneal to decrease its carbon content to less than 0.020% by weight.
2. A method for producing cold rolled rimmed steel sheet and strip having good drawability and stretchability represented by a conical cup value determined by the conical cup test specified by the Japanese Industrial Standard Z2249, said value being less than 37.30 for a sheet of the thickness of 0.8 mm. and dependent on a thickness selected from the range of 0.5 to 1.6 mm., comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.003-0.100% by Weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing anneal to decrease its carbon content to less than 0.020% by weight.
3. The method as claimed in claim 1, in which at least two elements selected from the group consisting of antimony, bismuth and niobium are added.
4. The method as claimed in claim 2, in which at least two elements selected from the group consisting of antimony, bismuth and niobium are added.
5. A method for producing cold rolled rimmed steel sheet and strip having good drawability and stretchability comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.003-0.100% by weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing and denitriding anneal to decrease its carbon content to less than 0.020% and its nitrogen content to less than 0.002%.
6. A method for producing cold rolled rimmed steel sheet and strip having good drawability and stretchability represented by a conical cup value determined by the conical cup test specified by the Japanese Industrial Standard Z-2249, said value being less than 37.30 for a sheet of the thickness of 0.8 mm. and dependent on a thickness selected from the range of 0.5 to 1.6 mm., comprising the steps of adding at least one element selected from the group consisting of antimony, bismuth and niobium to molten steel to produce a rimmed steel containing 0.003 0.100% by weight of said additive, making a cold rolled rimmed steel sheet or strip by hot and cold rolling procedure, and subjecting said steel sheet or strip to a decarburizing and denitriding anneal to decrease its carbon content to less than 0.020% and its nitrogen content to less than 0.002%.
7. The method as claimed in claim 5, in which at least two elements selected from the group consisting of antimony, bismuth and niobium are added.
8. The method as claimed in claim 6, in which at least two elements selected from the group consisting of antimony, bismuth and niobium are added.
9. The method according to claim 1 wherein the added element is antimony.
10. The method according to claim 1 wherein the added element is bismuth.
11. The method according to claim 1 wherein the added element is niobium.
12, The method according to claim 2 wherein the added element is antimony.
13. The method according to claim 2 wherein the added element is bismuth.
14. The method according to claim 2 wherein the added element is niobium.
15. A cold rolled decarburized rimmed steel sheet or strip having good drawability and stretchability, said steel consisting essentially of at least one element selected from the group consisting of antimony, bismuth and niobium, the total element percentage being 0.0030.100% by weight, less than 0.020% carbon, OAS-0.60% manganese, and the balance iron and incidental impurities.
16. The cold rolled steel sheet or strip according to claim 15 wherein at least two elements from the group consisting of antimony, bismuth and niobium are included in the steel.
17. The steel sheet or strip according to claim 15 wherein the nitrogen content of the steel is less than 0.002%.
18. The steel sheet or strip according to claim 16 wherein the nitrogen content of the steel is less than 0.002%.
References Cited by the Examiner UNITED STATES PATENTS 2,095,580 10/1937 Whetzel 14812 2,271,242 1/ 1942 Altenbwager 148-16 2,360,868 "10/1944 Gensamer 148-16 2,378,548 6/1945 Gregg -123 2,999,749 9/1961 Saunders et al. 7550 3,102,831 9/1963 Tisdale 148-12 3,105,780 9/1963 Low 148 16 OTHER REFERENCES Archiv fiir das Eisenhuttenwesen, vol, 8, 1934-35, pages 263 67.
DAVID L. RECK, Primary Examiner.
O. MARJAMA, Assistant Examiner.

Claims (1)

1. A METHOD FOR PRODUCING COLD ROLLED RIMMED STEEL SHEET AND STRIP HAVING GOOD DRAWABILITY AND STRETCHABILITY COMPRISING THE STEPS OF ADDING AT LEAST ONE ELEMENT SELECTED FROM THE GROUP CONSISTING OF ANTIMONY, BISMUTH AND NIOBIUM TO MOLTEN STEEL TO PRODUCE A RIMMED STEEL CONTAINING 0.003-0.100% BY WEIGHT OF SAID ADDITIVE, MAKING A COLD ROLLED RIMMED STEEL SHEET OR STRIP BY HOT AND COLD ROLLING PROCEDURE, AND SUBJECTING SAID STEEL SHEET OR STRIP TO A DECARBURIZING ANNEAL TO DECREASE ITS CARBON CONTENT TO LESS THAN 0.020% BY WEIGHT.
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US3404047A (en) * 1965-12-20 1968-10-01 United States Steel Corp Method for producing deep-drawing low-carbon steel sheet
US4204890A (en) * 1977-11-11 1980-05-27 Kawasaki Steel Corporation Method of producing non-oriented silicon steel sheets having an excellent electromagnetic property

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JPS5322052B2 (en) * 1971-12-27 1978-07-06

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US2095580A (en) * 1934-06-01 1937-10-12 American Sheet & Tin Plate Steel strip and its production
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US2378548A (en) * 1944-01-11 1945-06-19 Bethlehem Steel Corp Ferrous alloys containing bismuth
US2999749A (en) * 1958-09-17 1961-09-12 Union Carbide Corp Method for producing non-aging rimmed steels
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US2095580A (en) * 1934-06-01 1937-10-12 American Sheet & Tin Plate Steel strip and its production
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US2378548A (en) * 1944-01-11 1945-06-19 Bethlehem Steel Corp Ferrous alloys containing bismuth
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US3335036A (en) * 1964-01-25 1967-08-08 Kawasaki Steel Co Deep drawing steel sheet and method for producing the same
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