US20150376732A1 - Ferritic stainless steel sheet which is excellent in workability and method of production of same - Google Patents

Ferritic stainless steel sheet which is excellent in workability and method of production of same Download PDF

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US20150376732A1
US20150376732A1 US14/765,535 US201414765535A US2015376732A1 US 20150376732 A1 US20150376732 A1 US 20150376732A1 US 201414765535 A US201414765535 A US 201414765535A US 2015376732 A1 US2015376732 A1 US 2015376732A1
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steel sheet
workability
stainless steel
ferritic stainless
sheet
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Junichi Hamada
Eiichiro Ishimaru
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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Definitions

  • the present invention relates to ferritic stainless steel sheet which is excellent in workability and ridging resistance and a method of production of the same.
  • Ferritic stainless steel sheet is excellent in corrosion resistance and heat resistance and is being used for household electrical appliances, transport equipment, building use, and various other fields. However, it is inferior in ductility compared with austenitic stainless steel and suffers from formation of surface relief shapes called “ridging” when worked to shape it. There is therefore the problem of the surface quality and the polishing ability after being worked to shape it being obstructed.
  • ferritic stainless steel sheet can be improved in the “r-value”, an indicator of deep drawability, and improved in shapeability.
  • ridging occurs due to colonies of crystal grains which have similar crystal orientations remaining at the finished product sheet due to the casting structure or hot rolling structure.
  • numerous arts have been disclosed for reducing colonies which have ⁇ 100 ⁇ crystal orientations.
  • there are the electromagnetic stirring, inoculation of solidification nuclei, low temperature casting, etc. which are shown in PLT 2 etc. as techniques for making the solidified structure equiaxial.
  • limits on the hot rolling conditions, annealing conditions, and colony size in finished product sheet are known from PLTs 3 to 5 etc.
  • PLTs 6, 7, and 8 disclose patents relating to Sn-containing ferritic stainless steel.
  • PLT 7 discloses art relating to ferritic stainless steel which is excellent in corrosion resistance and workability and shows, relating to workability, art for giving Sn-containing steel a 0.2% yield strength of 300 MPa or less and elongation at break of 30% or more.
  • Sn-containing steel a 0.2% yield strength of 300 MPa or less and elongation at break of 30% or more.
  • 0.2% yield strength or elongation at break steel which is sufficiently satisfactory in deep drawability and ridging resistance cannot be obtained. Issues remain in workability.
  • PLT 1 Japanese Patent Publication No. 61-261460A
  • PLT 3 Japanese Patent Publication No. 61-1968882
  • PLT 5 Japanese Patent Publication No. 10-330887A
  • PLT 7 Japanese Patent Publication No. 2009-174036A
  • PLT 8 Japanese Patent Publication No. 2010-159487A
  • An object of the present invention is to solve the problems in the existing art and provide ferritic stainless steel sheet which is excellent in workability and which has little occurrence of ridging and a method of production of the same.
  • the inventors engaged in detailed studies relating to the workability and ridging resistance of ferritic stainless steel sheet, the steel composition, the formation of texture in the production process, and furthermore the mechanism of occurrence of ridging.
  • the gist of the present invention to solve the above problem is as follows:
  • a ferritic stainless steel sheet excellent in workability comprising, by mass %, Cr: 10 to 30%, Sn: 0.005 to 1%, C: 0.001 to 0.1%, N: 0.001 to 0.1%, Si: 0.01 to 3.0%, Mn: 0.01 to 3.0%, P: 0.005 to 0.1%, S: 0.0001 to 0.01% and a balance of Fe and unavoidable impurities, wherein an X-ray diffraction strength in the ⁇ 100 ⁇ 012> orientation from a surface layer of the steel sheet to t/4 is 2 or more, wherein “t” represents the sheet thickness.
  • the ferritic stainless steel sheet excellent in workability according to (1) further comprising, by mass %, one or more of Ti: 0.005 to 0.5%, Nb: 0.005 to 0.5%, Zr: 0.005 to 0.5%, V: 0.01 to 0.5%, Ni: 0.01 to 1%, Mo: 0.1 to 3.0%, W: 0.1 to 3.0%, Cu: 0.1 to 3.0%, B: 0.0003 to 0.0100%, Al: 0.01 to 1.0%, Ca: 0.0001 to 0.003%, Mg: 0.0001 to 0.005%, Co: 0.001 to 0.5%, Sb: 0.005 to 0.3%, REM: 0.001 to 0.2%, and Ga: 0.0002 to 0.3% or less.
  • a method of producing ferritic stainless steel sheet excellent in workability according to (1) or (2) comprising the steps of: heating a hot rolled steel sheet to 850° C. during annealing the steel sheet; cooling the steel sheet down to 500° C. by a cooling speed of 50° C./sec or less; and cold rolling the steel sheet using rolls of a diameter of 150 mm or less by a reduction rate of 60% or more.
  • FIG. 1 is a view which shows a relationship between a ⁇ 100 ⁇ 012> orientation strength at a surface layer of cold rolled annealed sheet down to t/4 and a ridging height.
  • Cr has to be added in 10% or more in order to secure corrosion resistance, high temperature strength, and oxidation resistance, but 30% or more addition causes deterioration of toughness and thereby poor manufacturability and also deterioration of quality. Accordingly, the range of Cr was made 10 to 30%. Furthermore, from the viewpoint of costs and corrosion resistance, 13.0 to 25.0% is desirable. Note that, if considering the manufacturability and high temperature ductility, 13.0 to 18.0% is desirable. 15.5 to 16.5% is also possible.
  • Sn is an extremely important element in the present invention for suppressing ridging by control of crystal orientation and is added in 0.005 to 1%.
  • Sn is an element which easily segregates at the grain boundaries. Grain boundary segregation occurs in the process of annealing hot rolled sheet in the production process. The inventors discovered that if cold rolling sheet and applying heat treatment for recrystallization, nuclei of a characteristic crystal orientation which is effective for reducing ridging easily form from the Sn segregated parts.
  • the ⁇ 111 ⁇ crystal orientation mainly grows.
  • the ⁇ 100 ⁇ orientation which is smaller in plastic deformation ability and more liable to result in reduction of sheet thickness than the ⁇ 111 ⁇ , is present in colonies, surface relief shapes will be formed after working and the ridging resistance will become poor.
  • the ⁇ 111 ⁇ crystal orientation becomes weak. In this research, it was discovered that when adding Sn, the ⁇ 100 ⁇ 012> orientation easily forms from the surface layer to near t/4 at the stage of annealing after cold rolling.
  • FIG. 1 shows the relationship between the ⁇ 100 ⁇ 012> orientation strength from the surface layer to near t/4 and the ridging resistance.
  • 17% Cr steel 0.005% C-0.1% Si—0.1% Mn-0.01% P-0.0001% S-0.1% Ti-0.18% Nb-0.007% N
  • Sn ⁇ 0.001%
  • the ⁇ 100 ⁇ 012> orientation X-ray diffraction strength was found by using an X-ray diffraction apparatus (made by Rigaku Corporation) and using Mo-K ⁇ -rays to obtain the (200), (310), and (211) pole figures of the region from the surface layer to near t/4 (measurement surface brought out by combination of mechanical polishing and electrolytic polishing) and using spherical harmonics to obtain the 3D crystal orientation density function from these and find the crystal orientation strength (ratio of strength with random sample).
  • a JIS No. 5 tensile test piece was taken from the cold rolled annealing sheet, given 16% strain in parallel to the rolling direction, and evaluated for ridging resistance by the ridging height (maximum distance of relief shapes occurring in direction perpendicular to rolling direction) and visual examination.
  • the ranks in the visual examination were as follows:
  • A Ridging not observed (ridging height 5 ⁇ m or less)
  • B Ridging observed somewhat visually (ridging height 10 ⁇ m or less)
  • C Ridging observed clearly visually (ridging height 20 ⁇ m)
  • D Ridging observed clearly visually and formation of relief shapes understood when touching surface by finger (ridging height over 30 ⁇ m)
  • the X-ray diffraction strength in the ⁇ 100 ⁇ 012> orientation from the surface layer to t/4 (“t” is sheet thickness) two times or more the ridging can become the A level and can be reduced to a level not posing a problem in practice. Therefore, the lower limit of the ⁇ 100 ⁇ 012> orientation strength was made 2 or more. That crystal orientation was obtained by grain boundary segregation of Sn and imparting shear strain in the above way. To make it formed more remarkably, it is necessary to increase the amount of grain boundary segregation of Sn or strengthen the shear strain. These sometimes are accompanied with issues in manufacturability and also lead to a fall in the r-value, so as a desirable range, the upper limit was made 10 or less.
  • the content should be as small as possible, therefore the upper limit was made 0.1%.
  • the lower limit was made 0.001%.
  • 0.002 to 0.05% is desirable.
  • making 0.002 to 0.009% is desirable.
  • Si is sometimes added as a deoxidizing element and also is an element which improves the oxidation resistance and high temperature strength. 0.01% or more is added. Excessive addition lowers the ordinary temperature ductility to degrade the workability, so the upper limit was made 3.0%. Furthermore, if considering the material quality and the oxidation characteristic, 0.05 to 1.0% is desirable. Furthermore desirable is 0.1 to 0.7%.
  • Mn forms MnCr 2 O 4 or MnO at a high temperature and improves the scale adhesion. This effect is manifested at 0.01% or more, so the lower limit was made 0.01%. On the other hand, excessive addition causes a drop in corrosion resistance and ductility, so the upper limit was made 3.0%. Furthermore, if considering workability and manufacturability, 0.05 to 1.5% is desirable. More desirably it is 0.1 to 1.0%.
  • P is a solution strengthening element in the same way as Si. Due to material quality, the smaller the content the better. The upper limit was made 0.1%. However, excessive reduction leads to an increase in the refining costs, so the lower limit was made 0.005%. Furthermore, if considering the manufacturing costs and oxidation resistance, 0.01 to 0.025% is desirable.
  • the upper limit was made 0.01%.
  • excessive addition forms compounds with Ti etc. and overly promotes the recrystallization and grain growth in the hot rolled annealed sheet to thereby degrade the r-value.
  • the lower limit was made 0.0001%.
  • 0.0010 to 0.0050% is desirable.
  • Ti is an element which is added for bonding with C, N, and S to further improve the corrosion resistance, grain boundary corrosion resistance, and deep drawability.
  • the growth of the ⁇ 111 ⁇ crystal orientation for improving the r-value is manifested by 0.005% or more of addition, so the lower limit was made 0.005%.
  • the toughness, secondary workability, and r-value deteriorate, so the upper limit was made 0.5%.
  • 0.05 to 0.2% is desirable.
  • Nb is an element which is added for improving the high temperature strength and high temperature fatigue characteristic by solution strengthening and precipitation strengthening. Further, it fixes C and N as carbonitrides, causes growth of the recrystallized texture of the finished product sheet, forms intermetallic compounds of Fe and Nb called “Laves phases”, has an effect on the formation of the recrystallized texture by its volume rate and size, and contributes to improvement of the r-value. These actions are manifested at 0.005% or more, so the lower limit was made 0.005%. On the other hand, excessive addition gives rise to hardening and leads to a drop in ordinary temperature ductility and r-value, so the upper limit was made 0.5%. Furthermore, if considering the costs and manufacturability, 0.1 to 0.3% is desirable.
  • Zr is an element which improves the oxidation resistance and is added in accordance with need. This action is manifested at 0.005% or more, so the lower limit was made 0.005%. However, 0.5% or more of addition causes the toughness and pickling ability and other aspects of manufacturability to become remarkably degraded. In addition, compounds of Zr with carbon and nitrogen become coarser to make the hot rolled annealed sheet structure coarser and lower the r-value, so the upper limit was made 0.5%. Furthermore, if considering the manufacturing costs, 0.05 to 0.20% is desirable.
  • V is an element which bonds with C and N to further improve the corrosion resistance, grain boundary corrosion resistance, and deep drawability.
  • growth of the ⁇ 111 ⁇ crystal orientation for improving the r-value is manifested by 0.01% or more addition, so the lower limit was made 0.01%.
  • the toughness and the secondary workability become degraded, so the upper limit was made 0.5%.
  • 0.05 to 0.3% is desirable.
  • Ni is an element which improves the toughness and corrosion resistance, so is added in accordance with need.
  • the contribution to toughness is manifested at 0.01% or more, so the lower limit was made 0.01%.
  • the upper limit was made 1%.
  • 0.05 to 0.5% is desirable.
  • 0.2 to 0.5% is more desirable.
  • Mo improves the corrosion resistance and causes an improvement of the high temperature strength due to the solid solution Mo. This effect is manifested at 0.1% or more, so the lower limit was made 0.1%.
  • excessive addition causes deterioration of the toughness and a drop in the elongation.
  • the Laves phases become overly formed, the ⁇ 011 ⁇ oriented grains are easily formed, and a drop in the r-value is caused.
  • the upper limit was made 3.0%.
  • 0.1 to 2.0% is desirable.
  • W in the same way as Mo, improves the corrosion resistance and causes an improvement of the high temperature strength due to the solid solution Mo. This effect is manifested at 0.1% or more, so the lower limit was made 0.1%.
  • excessive addition causes a deterioration of toughness and a drop in elongation.
  • the Laves phases are overly formed, the ⁇ 011 ⁇ oriented grains become easily formed, and a drop in the r-value is caused.
  • the upper limit was made 3.0%.
  • 0.1 to 2.0% is desirable.
  • Cu is an element which causes an improvement of the rust resistance and improves the high temperature strength, particularly in the medium temperature region, by precipitation of ⁇ -Cu.
  • the effect is manifested with 0.1% or more addition, so the lower limit was made 0.1%.
  • 3.0% or more addition deterioration of toughness and an extreme drop in the elongation are caused.
  • ⁇ -Cu precipitates in the hot rolling process whereby ⁇ 011 ⁇ oriented grains are formed and the r-value falls, so the upper limit was made 3.0%.
  • 0.2 to 1.5% is desirable. If considering the costs, 0.2 to 0.5% is good.
  • Al is sometimes added as a deoxidizing element and also improves the high temperature strength and oxidation resistance. This action is manifested from 0.01%, so the lower limit was made 0.01%. Further, 1.0% or more of addition causes a drop in the elongation and deterioration of the weldability and surface quality. In addition, Al oxides promote the formation of ⁇ 011 ⁇ oriented grains and lead to a drop in the r-value, so the upper limit was made 1.0%. Furthermore, if considering the refining costs, 0.02 to 0.15% is desirable.
  • Ca is sometimes added to immobilize the S. This effect is manifested at 0.0001% or more, so the lower limit was made 0.0001%. On the other hand, excessive addition causes the corrosion resistance to degrade, so the upper limit was made 0.003%. Furthermore, if considering the manufacturability and corrosion resistance, 0.0005 to 0.002% is desirable.
  • Mg forms Mg oxides together with Al in molten steel to act as a deoxidizing agent.
  • the finely crystallized Mg oxides form nuclei for fine precipitation of Nb- and Ti-based precipitates. If these finely precipitate in the hot rolling process, in the hot rolling process and hot rolled sheet annealing process, the fine precipitates form recrystallization nuclei whereby an extremely fine recrystallized structure is obtained. This contributes to formation of texture. This action is manifested from 0.0001%, so the lower limit was made 0.0001%. However, excessive addition causes degradation of the oxidation resistance and a drop in the weldability etc., so the upper limit was made 0.005%. Furthermore, if considering the refining costs, 0.0003 to 0.002% is desirable.
  • Co is an element which improves the high temperature strength. In accordance with need, 0.001% or more is added. However, excessive addition causes the workability to degrade, so the upper limit was made 0.5%. Furthermore, if considering the manufacturing costs, 0.05 to 0.3% is desirable.
  • Sb is effective for improving the corrosion resistance and may be added in 0.3% or more in accordance with need.
  • the lower limit is made 0.005.
  • 0.01% or more is preferable.
  • An REM is effective for improving the oxidation resistance and is added in accordance with need.
  • the lower limit is made 0.001%. Further, even if over 0.20% is added, the effect becomes saturated and the corrosion resistance falls due to the formation of grains of REM, so the upper limit is made 0.2%. If considering the workability of the finished product and the manufacturing costs, 0.002% to 0.05% is preferable.
  • Ga improves the corrosion resistance and suppresses hydrogen embrittlement, so 0.3% or less may be added.
  • the lower limit is made 0.0002%.
  • 0.0020% or more is preferable.
  • the inventors in addition to the above texture and chemical composition, the inventors also studied the method of production and learned that by controlling the hot rolled sheet annealing conditions and the cold rolling conditions, the distribution of crystal orientations can be controlled and excellent workability can be obtained.
  • the slab is hot rolled, then in general the hot rolled sheet is annealed to obtain a recrystallized structure.
  • the hot rolled sheet is annealed to obtain a recrystallized structure.
  • segregation of Sn at the crystal grain boundaries is promoted.
  • the material is heated to a 850° C. or more temperature, but at the cooling stage, the cooling speed down to 500° C. is made 50° C./sec or less to promote grain boundary segregation during this.
  • the heating temperature is less than 850° C.
  • a recrystallized structure cannot be obtained and a hot rolled orientation causing a drop in the band structure of the hot rolling or r-value remains, so the lower limit was made 850° C.
  • an upper limit of 1100° C. is desirable. If the objective is to obtain a recrystallized structure by annealing the hot rolled sheet, the upper limit value may be 1000° C. or less, more preferably the upper limit may be less than 900° C.
  • the cooling speed to make Sn sufficiently segregate, it is made 50° C./sec or less, but if considering maintaining the uniformity of the sheet shape, less than 15° C./sec is preferable. From the viewpoint of promoting grain boundary segregation of Sn as well, less than 15° C./sec is preferable.
  • excessively slow cooling lowers the manufacturability and also leads to a drop in the toughness of the hot rolled annealed sheet, so 5° C./sec or more is desirable. Further, for the reason of preventing a drop in toughness or deterioration of pickling ability due to precipitation of fine carbonitrides, over 10° C./sec is desirable. In the present invention, over 10° C./sec and less than 15° C./sec is desirable.
  • the sheet is rolled down to the predetermined sheet thickness.
  • rolls of a diameter of 150 mm or less are used and the reduction rate is made 60% or more. This is so as to give a sufficient shear strain to the Sn segregated part from the surface layer to the t/4 part.
  • the lower limit of the roll diameter is desirably made 30 mm.
  • the upper limit is desirably 95%.
  • the cold rolling roll diameter is desirably 30 to 100 mm and the reduction rate is desirably 75 to 90%.
  • the hot rolling conditions were a slab heating temperature of 1100 to 1250° C., a final temperature of 700 to 950° C., and a coiling temperature of 500° C. or less.
  • the annealing temperature was made 850 to 1100° C.
  • the cooling speed was made 11° C./sec.
  • ⁇ 60 mm rolls were used for rolling by a reduction rate of 80%.
  • the annealing of the cold rolled sheet was performed at 800 to 1000° C. to give a recrystallized structure in accordance with the steel components.
  • the thus obtained finished product sheets were evaluated for ridging resistance and ⁇ 100 ⁇ 012> orientation strength by the methods explained above. Further, they were evaluated for the indicator of deep drawability of the r-value.
  • the “r-value” is the average r-value obtained by obtaining JIS No. 13B tensile test pieces from the cold rolled annealed sheet, applying 14.4% strain in the rolling direction, the direction 45° to the rolling direction, and the direction 90° to the rolling direction, and using the formula (1) and formula (2).
  • W 0 is the sheet width before tension
  • W is the sheet width after tension
  • t 0 is the sheet thickness before tension
  • t is the sheet thickness after tension
  • r 0 is the r-value in the rolling direction
  • r 45 is the r-value in a direction 45° from the rolling direction
  • r 90 is the r-value in a direction perpendicular to the rolling direction
  • the average r-value need only be 1.5 or more to enable sufficient working.
  • steels which have the chemical compositions which are defined by the present invention are better in ridging resistance compared with comparative steels and have average r-values of high 1.5 or more.
  • the comparative examples have steel components which are outside the present invention, so they are steels where the finished product sheets have ⁇ 100 ⁇ 012> orientation strengths outside of the present invention, ridging resistance of the A rank cannot be obtained, and also the average r-values are less than 1.5.
  • the steels which are shown in Table 2 were evaluated for corrosion resistance by a wet/dry cycle test.
  • An outside diameter 15 mm, height 100 mm, thickness 0.8 mm test tube was filled with the test solution to 10 ml. To this, a 1 t ⁇ 15 ⁇ 100 mm (entire surface wet polished by #600 emery paper) sample was immersed. This test tube was placed in a 80° C. warm bath.
  • the steels of the present invention all had good maximum corrosion depths of 50 ⁇ m or less. Note that in the case of steels which contain Ni or Cu, the maximum corrosion depths were 15 ⁇ m or less, that is, extremely good results were shown in corrosion resistance. Further, Steel No. B8 with a content of Sn outside the range of components of the present invention had a corrosion depth of 50 ⁇ m, that is, was inferior in corrosion resistance compared with the invention examples.
  • the slab thickness, hot rolled sheet thickness, etc. may be suitably designed. Further, in the cold rolling, the reduction rate, roll roughness, roll diameter, rolling oil, number of rolling passes, rolling speed, rolling temperature, etc. may be suitably selected.
  • the annealing if necessary, may be bright annealing comprising annealing in hydrogen gas or nitrogen gas or other non-oxidizing atmosphere or may be annealing in the atmosphere. Furthermore, the elongation of the final temper rolling may be suitably adjusted or that rolling omitted. In addition, a tension leveler etc. may be used to correct the shape.
  • ferritic stainless steel sheet which is excellent in shapeability such as deep drawability and ridging resistance at a low cost without adding special facilities.

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