CN1039724C - Stainless steel sheet and method for producing thereof - Google Patents
Stainless steel sheet and method for producing thereof Download PDFInfo
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- CN1039724C CN1039724C CN94102539A CN94102539A CN1039724C CN 1039724 C CN1039724 C CN 1039724C CN 94102539 A CN94102539 A CN 94102539A CN 94102539 A CN94102539 A CN 94102539A CN 1039724 C CN1039724 C CN 1039724C
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- 239000010935 stainless steel Substances 0.000 title claims abstract description 66
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 65
- 238000004519 manufacturing process Methods 0.000 title abstract description 19
- 229910004298 SiO 2 Inorganic materials 0.000 claims abstract description 61
- 238000005097 cold rolling Methods 0.000 claims abstract description 55
- 238000000137 annealing Methods 0.000 claims abstract description 35
- 238000010438 heat treatment Methods 0.000 claims abstract description 26
- 238000000034 method Methods 0.000 claims abstract description 21
- 239000000203 mixture Substances 0.000 claims abstract description 15
- 230000008569 process Effects 0.000 claims abstract description 9
- 238000005554 pickling Methods 0.000 claims abstract description 5
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims abstract 21
- 238000010587 phase diagram Methods 0.000 claims abstract 3
- VASIZKWUTCETSD-UHFFFAOYSA-N manganese(II) oxide Inorganic materials [Mn]=O VASIZKWUTCETSD-UHFFFAOYSA-N 0.000 claims abstract 2
- 229910000734 martensite Inorganic materials 0.000 claims description 29
- 230000009467 reduction Effects 0.000 claims description 20
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 229910052681 coesite Inorganic materials 0.000 claims description 6
- 229910052906 cristobalite Inorganic materials 0.000 claims description 6
- 239000000377 silicon dioxide Substances 0.000 claims description 6
- 229910052682 stishovite Inorganic materials 0.000 claims description 6
- 229910052905 tridymite Inorganic materials 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 229910052760 oxygen Inorganic materials 0.000 claims description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 230000001590 oxidative effect Effects 0.000 claims description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims 2
- 229910052593 corundum Inorganic materials 0.000 claims 2
- 235000012239 silicon dioxide Nutrition 0.000 claims 2
- 229910001845 yogo sapphire Inorganic materials 0.000 claims 2
- 230000035882 stress Effects 0.000 description 69
- 239000000463 material Substances 0.000 description 60
- 229910000831 Steel Inorganic materials 0.000 description 26
- 238000005096 rolling process Methods 0.000 description 26
- 239000010959 steel Substances 0.000 description 26
- 229910001566 austenite Inorganic materials 0.000 description 25
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 24
- 230000007797 corrosion Effects 0.000 description 15
- 238000005260 corrosion Methods 0.000 description 15
- 238000005520 cutting process Methods 0.000 description 11
- 239000011651 chromium Substances 0.000 description 10
- 238000012360 testing method Methods 0.000 description 10
- 239000010949 copper Substances 0.000 description 9
- 239000010813 municipal solid waste Substances 0.000 description 9
- 239000011572 manganese Substances 0.000 description 8
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 8
- 239000000758 substrate Substances 0.000 description 7
- 238000005457 optimization Methods 0.000 description 6
- 238000004080 punching Methods 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- 230000032683 aging Effects 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000006243 chemical reaction Methods 0.000 description 3
- 239000002872 contrast media Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000004881 precipitation hardening Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000008021 deposition Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000010079 rubber tapping Methods 0.000 description 2
- 239000002893 slag Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 238000007669 thermal treatment Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 240000004859 Gamochaeta purpurea Species 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical group [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000008485 antagonism Effects 0.000 description 1
- 230000002968 anti-fracture Effects 0.000 description 1
- 238000003556 assay Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 230000000875 corresponding effect Effects 0.000 description 1
- 125000004122 cyclic group Chemical class 0.000 description 1
- 230000003467 diminishing effect Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Images
Classifications
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- 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
- C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
-
- 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
- C21D9/24—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for saw blades
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
一种抗断裂性的不锈钢板包含：不可避免地存在于不锈钢中的Al2O3、MnO与SiO2非金属夹杂物；该非金属夹杂物具有位于由“Al2O3-MnO-SiO2”三元系相图中的九个点规定范围内的组成；该不锈钢板具有至少1520N/mm2(155kgf/mm2)的1.0%起始应力；196N/mm2(20kgf/mm2)或更低的1.0%起始应力的各向异性差；以及至少4.6mm的杯突深度值。其制造方法包括：制取不锈钢带；对该不锈钢带施加退火-酸洗-第一次冷轧-第一次中间退火-第二次冷轧-第二次中间退火-第三次冷轧-最终退火-第四次冷轧-低温热处理的过程。A fracture-resistant stainless steel plate includes : Al 2 O 3 , MnO and SiO 2 non-metallic inclusions that inevitably exist in stainless steel; the non-metallic inclusions have "A composition within the specified range of nine points in the ternary system phase diagram; the stainless steel plate has a 1.0% initial stress of at least 1520N/mm 2 (155kgf/mm 2 ); 196N/mm 2 (20kgf/mm 2 ) or A lower anisotropy difference of 1.0% initial stress; and a cupping depth value of at least 4.6 mm. The manufacturing method includes: preparing stainless steel strip; applying annealing to the stainless steel strip - pickling - the first cold rolling - the first intermediate annealing - the second cold rolling - the second intermediate annealing - the third cold rolling - The process of final annealing-the fourth cold rolling-low temperature heat treatment.
Description
The present invention relates to a kind of stainless steel plate and manufacture method thereof of resistance to fracture, relate in particular to a kind of stainless steel and manufacture method thereof as internal diameter saw blade (innerdiameter saw blades) substrate, for example, this saw blade is used for silicon ingot is cut into silicon chip.
So far, mainly use metastable austenite stainless steel and precipitation hardening (pH) stainless steel as the base mateiral that is used for internal diameter saw blade substrate.Generally by the metastable austenite stainless steel of SUS301.5SUS304 representative be by the cold working after the annealing firmly than and shaping is processed to form martensitic phase and further timeliness obtains high-intensity.JP-B-2-44891 (term that relates to herein " JP-B-" expression " the Japanese patent laid-open publication gazette communique of having examined ") discloses a kind of technology of relevant this types of steel.According to above-mentioned disclosed technology, contain controlled composition to obtain a kind of steel plate of required austenite phase stability degree, with 40% or higher draft carry out first time before temper rolling (temperrolling) and the pinch pass with for the second time cold rolling, wherein for the first time cold rolling with for the second time cold rolling ratio is 0.8 or bigger.This technological process is intended to by obtaining 1275N/mm
2Or higher tensile strength reduces to minimum and planeness steel during the improvement tension with the in-plane anisotropy difference that makes intensity (0.2% proof stress).
The exemplary embodiments of PH Stainless Steel is SUS631.Cold working or (under the zero degree) subzero treatment by the back steel of annealing have produced martensitic stucture or austenite and martensitic duplex structure.In the successive ageing treatment,, precipitation hardening obtains high strength thereby taking place.In JP-A-61-295356 and JP-A-63-317628 (term that relates to " JP-A-" expression " the open communique of uncensored Japanese Patent "), introduced such steel herein.According to these patents, precipitation hardening takes place to obtain the high rigidity of Hv=580 by adding Si and Cu.In addition, high crack stress (cracking stress) and improvement tension performance have also been obtained.
For improving the slice surface quality and making ingot cutting loss reduce to the minimum planeness that must guarantee the internal diameter saw blade.For suppress on the saw blade local stress intensity so that during the section saw blade fracture reduce to minimum, also must guarantee the accurate garden degree of internal diameter saw blade.For further improving the rigidity of internal diameter saw blade, during cutting into slices, on the Zhou Fangxiang of garden, saw blade is applied pulling force (abbreviating " tension " below as (tensioning)).Particularly, reduce the saw blade vibration by raising saw blade rigidity and become the requisite measure of boosting productivity to reduce ingot cutting loss.Therefore, require to give saw blade high rigidity by during straining, on the Zhou Fangxiang of garden, applying 1.0% high strain.
Yet there are some characteristics in conventional stainless saw blade, and they obtain through being everlasting just to rupture before enough tensions, also rupture during sectioning even have the saw blade of good tension performance.
In JP-B-2-44891, considered the in-plane anisotropy of intensity, but do not considered fracture characteristics fully.In JP-A-61-295356 and JP-A-63-317628, the intensity before will having strained is brought up to a certain degree, but does not consider the fracture during the section of tension back fully.Under the high strained condition of strain size about 1.0%, two kinds of technical antagonism breaking properties all do not have improved action during straining.In fact, the stainless steel plate that uses in above-mentioned three kinds of prior arts all demonstrates high tensile strength, but the deformation stress when applying 1.0% strain (abbreviating " 1.0% initial stress (On-set stress) " hereinafter as) is low, or toughness is low.Therefore, use the internal diameter saw blade of these materials during straining, often to rupture, also during sectioning, rupture even they have good tension performance.
The object of the present invention is to provide a kind of stainless steel plate and manufacture method thereof with high resistance to fracture.
To achieve these goals, the invention provides a kind of stainless steel plate of high resistance to fracture, this stainless steel plate comprises:
Be present in the Al in the stainless steel inevitably
2O
3, MnO and SiO
2Non-metallic inclusion;
This non-metallic inclusion has and is positioned at by " Al
2O
3-MnO-SiO
2" composition in following nine some specialized ranges of providing by weight percentage in the three component system phasor,
Point 1 (Al
2O
3: 21%, MnO:12%, SiO
2: 67%),
Point 2 (Al
2O
3: 19%, MnO:21%, SiO
2: 60%),
Point 3 (Al
2O
3: 15%, MnO:30%, SiO
2: 55%),
Point 4 (Al
2O
3: 5%, MnO:46%, SiO
2: 49%),
Point 5 (Al
2O
3: 5%, MnO:68%, SiO
2: 27%),
Point 6 (Al
2O
3: 20%, MnO:61%, SiO
2: 19%),
Point 7 (Al
2O
3: 27.5%, MnO:50%, SiO
2: 22.5%),
Point 8 (Al
2O
3: 30%, MnO:38%, SiO
2: 32%),
Point 9 (Al
2O
3: 33%, MnO:27%, SiO
2: 40%),
Described stainless steel plate has 1520N/mm
2(155kgf/mm
2) or 1.0% higher initial stress, wherein 1.0% initial stress is the deformation stress when bearing 1.0% strain.
Described stainless steel plate has 196N/mm
2(20kgf/mm
2) or the anisotropy of lower 1.0% initial stress poor, wherein the anisotropy difference is the absolute value of the difference of 1.0% initial stress on the perpendicular direction of rolling direction;
Described stainless steel plate has the Erichsen number of 4.6mm at least.
Described stainless steel plate is grouped into by following one-tenth basically, by weight:
0.1-0.2%C, 0.1-2%Si, 0.1-2%Mn, 4-11%Ni, 13-20%Cr, 0.01-0.2%N, 0.0005-0.0025% solubility Al, 0.002-0.013%O, 0.08-0.9%Cu is no more than 0.009%S, and the Fe of surplus.
According to a preferred embodiment of the present invention, the C content of described stainless steel plate is 0.032-0.178 weight %.
According to a preferred embodiment of the present invention, the Si content of described stainless steel plate is 0.21-1.85 weight %.
According to a preferred embodiment of the present invention, the Mn content of described stainless steel plate is 0.49-1.80 weight %.
According to a preferred embodiment of the present invention, the Ni content of described stainless steel plate is 5.12-8.80 weight %.
According to a preferred embodiment of the present invention, the Cr content of described stainless steel plate is 13.9-16.8 weight %.
According to a preferred embodiment of the present invention, the N content of described stainless steel plate is 0.012-0.190 weight %.
According to a preferred embodiment of the present invention, the solubility Al content of described stainless steel plate is 0.0006-0.0023 weight %.
According to a preferred embodiment of the present invention, the O content of described stainless steel plate is 0.0032-0.0120 weight %.
According to a preferred embodiment of the present invention, the Cu content of described stainless steel plate is 0.12-0.35 weight %.
According to a preferred embodiment of the present invention, wherein said non-metallic inclusion contains 13-24%Al by weight
2O
3, 27-49%MnO and 34-55%SiO
2
In addition, the invention provides a kind of method of making high resistance to fracture stainless steel plate, this method may further comprise the steps:
Produce basically by following elementary composition Stainless Steel Band, by weight: the Cu of O, the 0.08-0.9% of solubility Al, the 0.002-0.013% of N, the 0.0005-0.0025% of Cr, the 0.01-0.2% of Ni, the 13-20% of Mn, the 4-11% of the C of 0.01-0.2%, the Si of 0.1-2%, 0.1-2%, 0.009% or lower S, all the other are Fe and unavoidable impurities;
Described unavoidable impurities exists with the non-metallic inclusion form, and these inclusiones have and are positioned at by " Al
2O
3-MnO-SiO
2" composition in following nine some specialized ranges of providing by weight percentage in the three component system phasor,
Point 1 (Al
2O
3: 21%, MnO:12%, SiO
2: 67%),
Point 2 (Al
2O
3: 19%, MnO:21%, SiO
2: 60%),
Point 3 (Al
2O
3: 15%, MnO:30%, SiO
2: 55%),
Point 4 (Al
2O
3: 5%, MnO:46%, SiO
2: 49%),
Point 5 (Al
2O
3: 5%, MnO:68%, SiO
2: 27%),
Point 6 (Al
2O
3: 20%, MnO:61%, SiO
2: 19%),
Point 7 (Al
2O
3: 27.5%, MnO:50%, SiO
2: 22.5%),
Point 8 (Al
2O
3: 30%, MnO:38%, SiO
2: 32%),
Point 9 (Al
2O
3: 33%, MnO:27%, SiO
2: 40%),
This stainless steel plate is applied cold rolling (CR annealing-pickling-first time
1Process annealing-the second time of)-for the first time cold rolling (CR
2Process annealing-cold rolling for the third time (the CR of)-for the second time
3Four cold rolling (CR of)-final annealing-Di
3)-low temperature heat treatment;
Cold rolling, the described second time of the described first time, cold rolling and described cold rolling for the third time draft respectively was 30%-60%;
Described the 4th cold rolling draft is 60-76%, and the 4th time every time cold rolling draft is 3-15%;
Annealing temperature in the described annealing first time, annealing for the second time and final annealing respectively is respectively 950 °-1100 ℃;
Carry out the 0.1-300 described low-temperature heat treatment of second 300 ° of-600 ℃ of temperature;
Containing 70 volume % or higher H
2Nonoxidizing atmosphere in carry out described final annealing and described low-temperature heat treatment.
Fig. 1 is expression " Al
2O
3-MnO-SiO
2" figure of inclusion compositing range of the present invention in the three component system phasor;
Fig. 2 is the curve of the measuring method of expression 1.0% initial stress;
Fig. 3 is illustrated in 196N/mm
2(20kgf/mm
2) or the condition of the anisotropy difference of lower 1.0% initial stress under, 1.0% initial stress and Erichsen number are to the figure of resistance to fracture influence of the present invention;
Fig. 4 is illustrated in greater than 196N/mm
2(20kgf/mm
2) the anisotropic condition of 1.0% initial stress under, 1.0% initial stress and Erichsen number are to the figure of resistance to fracture influence of the present invention;
Fig. 5 is the figure that expression 1.0% initial stress and martensite quantity influence resistance to fracture of the present invention.
Inventors are to making the various mechanical properties such as the poor and toughness of distortional stress, in-plane anisotropy under Young's modulus, about 1.0% strain, and form and the optimization of creating conditions has been carried out a series of broad research, to obtain these mechanical performances, inventors have found the understanding of following relevant corrosion resistant plate, and this corrosion resistant plate demonstrates high resistance to fracture to have simultaneously good tension performance and have high resistance to fracture under tension stage and section stage.
(1) for improve during the saw blade tension with section during resistance to fracture, thickness and quantity and the high field trash of introduction ductility that minimizing certainly will become the non-metallic inclusion of fracture origin all are effective measures. For this reason, the inevitable non-metallic inclusion that exists forms and must comprise Al in stainless steel2O
3, MnO and SiO2, and these field trashes must be positioned at by " Al2O
3-MnO-SiO
2" in nine points (1-9) of providing in ternary system phasor scope of surrounding.
(2) in order to improve the resistance to fracture during the tension, require to make to determine toughness and the Young's modulus optimization of tensile property and the non-metallic inclusion described in the control (1). In other words, require 4.6mm or larger Erichsen number, and Young's modulus is preferably 166,600N/mm2(17,000kgf/mm
2) or higher.
(3) in order to improve the resistance to fracture during the saw blade sectioning, in the non-metallic inclusion described in the control (1), also require to make the balance optimization between the poor and toughness of the in-plane anisotropy of 1.0% initial stress, 1.0% initial stress. In other words, 1.0% initial stress is 1520N/mm2(155kgf/mm
2) or anisotropy higher, 1.0% initial stress poor (rolling direction with perpendicular to rolling direction on the absolute value of difference of 1.0% initial stress) be 196N/mm2(20kgf/mm
2) or lower and Erichsen number be 4.6mm or more mostly be necessary.
(4) have with the manufacturing of metastable austenite stainless steel in the corrosion resistant plate situation of above-mentioned material characteristic, must control the non-metallic inclusion described in (1), make the martensite quantity optimization under the composition requirement and make the Effective grain size size reduce to minimum and homogenising. Specifically, should comprise the martensite content of 40-90% with the internal diameter saw blade of corrosion resistant plate manufacturing, the stainless steel band that wherein mainly is comprised of mentioned component is through comprising cold rolling, the intermediate annealing of annealing, pickling, for the first time cold rolling, intermediate annealing, the second time, the manufacture process of the cold rolling and Low Temperature Heat Treatment of cold rolling, final annealing, the 4th time for the third time. In this technical process, should meet the following conditions. Respectively be 30%-60% with cold rolling for the third time reduction ratio for the second time for the first time; The 4th time cold rolling (temper rolling) reduction ratio is 60-76%; And every time reduction ratio (the 4th cold rolling reduction ratio is divided by the road number of times) is 3.0-15%; Containing 70 volume % or higher H2Nonoxidizing atmosphere in carry out final annealing and Low Temperature Heat Treatment; In 950 ° of-1150 ℃ of temperature ranges, carry out centre and final annealing; And carry out 1-300 timeliness second.
The reason that below is described in detail the present invention and limits each condition.
The basic material that is used for internal diameter saw blade substrate must be made by stainless steel, because they should have enough corrosion resistancies during slicing silicon ingots. Because being used for the basic material of internal diameter saw blade substrate is a kind of sheet material (thickness is generally 0.3mm or thinner) as thin as a wafer, reduction certainly will become fracture origin non-metallic inclusion thickness and quantity and to make these field trashes have good ductility be effective with the raising resistance to fracture. Specifically, inevitably the composition of non-metallic inclusion must comprise Al2O
3, MnO and SiO2, this composition is included in " Al shown in Figure 12O
3-MnO-SiO
2" in following nine some lines of providing by weight percentage in ternary system phasor scope of surrounding,
Point 1 (Al2O
3：21％，MnO：12％，SiO
2：67％)，
Point 2 (Al2O
3：19％，MnO：21％，SiO
2：60％)，
Point 3 (Al2O
3：15％，MnO：30％，SiO
2：55％)，
Point 4 (Al2O
3：5％，MnO：46％，SiO
2：49％)，
Point 5 (Al2O
3：5％，MnO：68％，SiO
2：27％)，
Point 6 (Al2O
3：20％，MnO：61％，SiO
2：19％)，
Point 7 (Al2O
3：27.5％，MnO：50％，SiO
2：22.5％)，
Point 8 (Al2O
3：30％，MnO：38％，SiO
2：32％)，
Point 9 (Al2O
3：33％，MnO：27％，SiO
2：40％)，
By with Al in the non-metallic inclusion2O
3, MnO and SiO2Between ratio of components be limited in the prescribed limit, can improve resistance to fracture.
For the field trash that obtains above regulation forms, the preferred use by containing 50% or the ladle made of the MgO-CaO of lower CaO and contain [Cao]/[SiO in the refining in the bucket after tapping2]=1.0-4.0,3% or lower Al2O
3, 15% or the CaO-SiO of lower AgO and 30-80%CaO2-Al
2O
3Slag.
Inventors find that for the corrosion resistant plate as the internal diameter saw blade, Young's modulus, 1.0% initial stress and Erichsen number are the key factors of resistance to fracture.
Fig. 2 illustrates the assay method of 1.0% initial stress. In stress one strain figure, cause the distortional stress of 1.0% strain to be called as 1.0% initial stress (On-Sete tress). As mentioned above, under tension condition and ingot section load, the internal diameter saw blade bears high-tensile strength corresponding to 1.0% strain size at garden Zhou Fangxiang. Therefore, estimating 1.0% initial stress is effective for measuring resistance to fracture.
Fig. 3 and Fig. 4 show 1.0% initial stress and Erichsen number to the impact of resistance to fracture. Fig. 3 shows 196N/mm2(20kgf/mm
2) or the poor condition of anisotropy of lower 1.0% initial stress under situation, Fig. 4 shows greater than 196N/mm2(20
kgf/mm
2) the poor condition of anisotropy of 1.0% initial stress under situation. Two figures only show has 166,600N/mm2(17,000kgf/mm
2) or more high Young's modulus and the well material of tension performance. Young's modulus can change the pulling force size that puts on saw blade because of tension, for obtaining good tension performance, 166,600N/mm2(17,
000kgf/mm
2) or higher Young's modulus be necessary. If Young's modulus is lower than 17,000kgf/mm2, then straining the pulling force that requires to impose on saw blade increases significantly, and this can reduce resistance to fracture.
According to Fig. 3, in being lower than the Erichsen number scope of 4.6mm, material will be during straining fracture. On the other hand, at 4.6mm or larger Erichsen number be lower than 1520N/mm2(155kgf/mm
2) 1.0% initial stress scope in, will be during cutting into slices fracture. At 4.6mm or larger Erichsen number and 1520N/mm2(155
kgf/mm
2) or higher 1.0% initial stress scope in, this material neither can be during straining can be during not cutting into slices yet fracture.
The anisotropy of 1.0% initial stress is poor greater than 196N/mm2(20kgf/mm
2) all material all can fracture, this is illustrated among Fig. 4. Larger anisotropy is poor will to be increased owing to tension makes the difference of garden Zhou Fangxiang upper pulling force. As a result, thus in plane of saw blade, cause inhomogeneities fracture during cutting into slices of significant pulling force. So the in-plane anisotropy of basic material intensity is poor preferably as much as possible little. As shown in Figure 3, as the poor 196N/mm that is maintained at of the anisotropy of 1.0% initial stress2(20kgf/mm
2) or when lower, then in the punch test merit of regulation and 1.0% initial stress scope, can obtain fabulous resistance to fracture.
From above discussion, the present invention will prevent that basic material necessary mechanical performance of fracture during straining or during cutting into slices is defined as: 1.0% initial stress: 1520N/mm2(155kgf/mm
2) or higher; The anisotropy of 1.0% initial stress is poor: 196N/mm2(20kgf/mm
2) or lower: Erichsen number: 4.6mm or higher. Although the Erichsen number condition of 4.6mm will be given good tension performance, from finishing thousands of inferior ingot section viewpoints, in order further to improve the preferred 4.6mm of resistance to fracture or larger Erichsen number.
The metastable austenite stainless steel is a kind of as in the basic material stainless steel of above-mentioned internal diameter saw blade substrate corrosion resistant plate. Below narrate condition and the reason thereof of the stainless composition of metastable austenite and manufacturing process.
Each composition of following provisions and content thereof.
Carbon is a kind of element that forms the austenite phase, and helps to suppress the solid solution that δ-ferritic phase formed and strengthened martensitic phase. Yet the C concentration that is lower than 0.01 % by weight can not produce abundant effectiveness, and will cause the carbide precipitation of Cr and reduce corrosion resistance and toughness above the C of 0.2 % by weight. Therefore, C content is defined as the 0.01-0.2 % by weight.
Manganese also is a kind of element that forms the austenite phase. Need 0.1 % by weight or higher Mn content in order to form austenite one phase and deoxidation by solution heat treatment. Yet when Mn content surpassed 2.0 % by weight, austenite was met and is become undue stable, and this can greatly suppress the formation of martensitic phase. Therefore, the Mn content range is defined as the 0.1-2.0 % by weight.
Nickel is a kind of element that forms strong austenite phase. When Ni content is lower than 4.0 % by weight, after annealing, can not produce single-phase austenite. On the other hand, when Ni content was higher than 11 % by weight, austenite was met and is become undue stable, and this can greatly suppress the formation of martensitic phase. Therefore, the Ni content range is defined as the 4.0-11 % by weight.
Chromium is the requisite element of a kind of stainless steel. In order to obtain enough corrosion resistancies, Cr content must be 13.0 % by weight or higher. Yet 20.0 % by weight or higher Cr content can produce a large amount of δ-ferritic phases when high temperature, and this can reduce hot-workability. Therefore, the Cr content range is defined as the 13.0-20.0 % by weight.
Nitrogen is a kind of element that forms the austenite phase, also helps to strengthen the solid solution of martensitic phase. The N content that is lower than 0.01 % by weight can not produce effectiveness, and the N content that is higher than 0.20 % by weight can produce pore during casting. Therefore, the N content range is defined as 0.01-0.20 % by weight.
Aluminium (solubility Al) content determines number and the composition of non-metallic inclusion. When solubility Al content was lower than 0.0005 % by weight, the oxygen content of molten steel surpassed 0.013 % by weight so that produces MnO and SiO2The field trash that content is high and high boiling field trash (Cr for example2O
3), this will reduce widely the hot-workability of steel and increase the possibility of saw blade fracture. On the other hand, when solubility Al content surpassed 0.0025 % by weight, the O content in the molten steel became and is lower than 0.002 % by weight, and the number of field trash also reduces. Yet, in latter instance, a large amount of Al have appearred containing2O
3Field trash, this can cause blemish and increase the possibility of saw blade fracture. So, in order in steel, to have the as shown in Figure 1 Al of low melting point high-temperature ductility2O
3-MnO-SiO
2Be non-metallic inclusion, further field trash thickness attenuation and reduce the field trash number, solubility Al content must be defined in the 0.0005-0.0025 % by weight scope and with O content to be defined in 0.002-0.013 % by weight scope.
Copper is a kind of element as the necessary reinforcement passive state of internal diameter saw blade superficial layer and raising corrosion resistance. However, the Cu content that is lower than 0.08 % by weight can not demonstrate enough effectiveness. Yet the Cu content that is higher than 0.90 % by weight makes this effectiveness be in saturation state, and has been reduced hot-workability owing to Cu does not stay austenite fully admittedly in mutually. Therefore, the scope of Cu content is defined as the 0.08-0.90 % by weight.
Silicon is a kind of element that helps to strengthen austenite phase and martensitic phase solid solution. The Si content that is lower than 0.1 % by weight can not produce abundant effectiveness, thereby the Si content that is higher than 2.0 % by weight forms δ-ferritic phase reduction hot-workability. Therefore, the Si content range is defined as the 0.1-2.0 % by weight.
Sulphur forms for example MnS field trash. These field trashes certainly will become the fracture origin of saw blade. Particularly, thus the S content that is higher than 0.0090 % by weight can reduce toughness increases the fracture possibility. Therefore, the S upper content limit is defined as 0.0090 % by weight.
Except mentioned component, metastable austenite corrosion resistant plate of the present invention can also suitably comprise Ca and the rare earth metal (REM) that is intended to control oxide morphology and improves processability, and the B or other element that are intended to improve hot-workability. Add these elements and can not affect essential characteristic of the present invention.
Inventors study in great detail for the material factor that improves 1.0% initial stress in the metastable austenite stainless steel situation, and find that it is necessary making the martensitic phase quantity optimization under the above-mentioned condition. Fig. 5 shows 1.0% initial stress and martensite quantity to the impact of resistance to fracture. This figure only shows that the anisotropy that satisfies 1.0% initial stress is poor, the various materials under the suitable condition of Young's modulus and punch test merit. According to Fig. 5, must be by making cold rolling condition and aging condition optimization assurance 40% or more martensite quantity to obtain 1520N/mm2(155kgf/mm
2) or 1.0% larger initial stress. On the other hand, when martensite quantity surpassed 90%, the punch test merit significantly reduced, and the possibility that ruptures during the tension greatly increases. So the martensite content that is applied to inside diameter saw bar thickness of slab place is defined as 40-90%. In Fig. 5, have the martensite quantity of 40-9 0% and have the 1520N/mm of being lower than2(155kgf/mm
2) the material of 1.0% initial stress be contrast material No.19 and No.22, they are narrated afterwards.
Below give an account of the manufacture method of steady stainless sheet steel in the narration. Stainless steel band with above-mentioned chemical composition is carried out following a series of processing.
Annealing and pickling-first time are cold rolling-intermediate annealing-second time is cold rolling-intermediate annealing-for the third time cold rolling-containing 70 volume % or more H2Nonoxidizing atmosphere in final annealing-the 4th time cold rolling-containing 70 volume % or more H2Nonoxidizing atmosphere in Low Temperature Heat Treatment.
Repeat cold rolling and anneal cycles process and cause forming thinner recrystallization texture in each annealing, in some cases, by making martensitic phase behind the temper rolling (the 4th time is cold rolling) the thinner superfine carbide particle Uniform Dispersion that strengthens that becomes. As a result, improved 1.0% initial stress and punch test merit, and made texture become unordered type, this also makes poor the diminishing of anisotropy of 1.0% initial stress. So, preferably repeatedly repeat cold rolling and the anneal cycles process. Yet, repeat too much this cyclic process and make production line complicated and make this effectiveness saturated. So be chosen as three times with the number of repetition anneal cycles process cold rolling, carry out subsequently temper rolling (the 4th time cold rolling).
For the first time cold rolling, cold rolling and when cold rolling reduction ratio all is lower than 30% respectively for the third time, because the mixing texture after the annealing certainly will produce the heterogeneity material for the second time. When these rolling reduction ratios surpass 60%, make grain size number reduce to the minimum effectiveness state that reaches capacity, thereby this texture become and has too firmly increased in-plane anisotropy, rolling load has also increased, and this will reduce operability. Therefore, for the first time cold rolling, for the second time cold rolling and for the third time cold rolling reduction ratio be chosen as 30-60%.
The reason of finish rolling or the 4th cold rolling selection 60-76% reduction ratio is that the martensite quantity in especially being used in the 40-90% scope improves 1.0% initial stress, when reduction ratio 60% when following, martensite quantity becomes and is lower than 40%, and the size of Young's modulus or 1.0% initial stress not. On the other hand, when reduction ratio 7 6% when above, martensite quantity surpasses 90%, Young's modulus and 1.0% initial stress increase, but Erichsen number reduces, this can not cause the firm balance between the strength and toughness.
Every time reduction ratio during the temper rolling (determining this reduction ratio divided by the road number of times by the finish rolling reduction ratio) is when being lower than 3.0%, and Erichsen number reduces, and production cost improves owing to rolling number of times increases. When reduction ratio surpasses 15%, the poor increase of the anisotropy of 1.0% initial stress, and Erichsen number is owing to discontinuity of material reduces. Therefore, every time reduction ratio is defined as 3.0-15% during the finish rolling.
Carry out Low Temperature Heat Treatment to improve 1.0% initial stress and other characteristic. Low Temperature Heat Treatment below 300 ℃ or 300 ℃ can not get enough effects, can not improve 1.0% initial stress. On the other hand, will cause the reverse conversion austenite phase of remarkable quantity in the Low Temperature Heat Treatment temperature more than 600 ℃ or 600 ℃, this can reduce by 1.0% initial stress and other characteristic. Therefore, the temperature of Low Temperature Heat Treatment is defined as 300 ℃-600 ℃. About the aging time in the set point of temperature scope, the time that is less than 1 second does not reach enough effects, and expectation can not improve 1.0% initial stress. Do not go out the effect of further improvement characteristic more than 300 seconds Low Temperature Heat Treatment time showing. Particularly, reverse conversion austenite phase occurred significantly near 600 ℃ temperature province the time, this can reduce by 1.0% initial stress and other characteristic. Therefore, the Low Temperature Heat Treatment time is defined as 1-300 second. By in 400 ℃ of-500 ℃ of temperature ranges, carrying out the 2-15 Low Temperature Heat Treatment of second, can expect further to improve various characteristics.
When in oxidizing atmosphere, carrying out final annealing or Low Temperature Heat Treatment, then need acid pickling step. The pickling meeting produces grain boundary corrosion at surface of steel plate, and corrosion hinders sheet material to obtain essential resistance to fracture and corrosion resistance. When these heat treatments are to be lower than 70 volume %H containing2Nonoxidizing atmosphere in when carrying out, can produce deposition at surface of steel plate, this can hinder steel plate to obtain essential anti-fracture and erosion-resisting quality. Therefore, 70 volume % or higher H should contained2Nonoxidizing atmosphere in carry out final annealing and Low Temperature Heat Treatment.
According to above-mentioned various conditions, just can produce a kind ofly have high strength, the extremely low simultaneously steady quality of fracture possibility, little in-plane anisotropy is poor and the corrosion resistant plate that is used for internal diameter saw blade substrate of toughness.
The present invention is used for the stainless steel plate of internal diameter saw blade, also can use martensite pH stainless steel, austenite pH stainless steel and metastable austenite pH stainless steel except the metastable austenite stainless steel.Production is used for the steel plate that the stainless base steel plates of internal diameter saw blade substrate of the present invention also can be used the casting thin plate and produce with these casting thin plates.
Embodiment
Carry out melting to produce ingot to having the steel of forming shown in the table 1, this ingot carries out the cogging breaking down, carries out the hot rolling processing to produce band then.Each steel of A-H are steel of the present invention, and each steel of I-M are to be used for correlated steel.Other all steel except I, J, L and M all are to use between refining period in the bucket after tapping and contain 50% or the steel teeming ladle of the MgO-CaO refractory materials manufacturing of lower CaO, and use to have and consist of [CaO]/[SiO
2]=1.0-4.0 (weight), 3% or lower Al
2O
3, 15% or the CoO-SiO of lower MgO and 30-80%CaO
2-Al
2O
3Slag is produced.When possessing above-mentioned those conditions, the main inclusions of appearance is that fusing point is 1400 ℃ or lower Al
2O
3-MnO-SiO
2On the other hand, for the steel K that contains a large amount of S, Al
2O
3-MnO-SiO
2Though the fusing point of inclusion is 1400 ℃ or lower, the various sulfide of huge amount have been comprised.
According to creating conditions that table 2 and table 3 are listed, produce each hot rolled strip to produce the No.1-No.29 material.Among these materials, No.1-No.15 is a material of the present invention, and No.16-No.29 is a contrast material.The No.1-No.15 material is the material of producing with the A-H steel of the present invention, they contain the non-metallic inclusion with low melting point and good high-temperature ductility, this inclusion can spread on rolling direction well, and most of inclusiones all are 5 μ m or equally thin thin shape thing below the 5 μ m.Table 4-table 6 shows the evaluation of martensite quantity, each mechanical characteristics and resistance to fracture to each material of No.1-No.29.
Be given in below that plane difference of hardness, anisotropy used in the table 4-table 6 are poor, the definition of punching test merit load and resistance to fracture.
The plane difference of hardness is the absolute value of the difference of highest hardness and minimum hardness in the saw blade plane.
The anisotropy difference is the absolute value of the difference of 1.0% initial stress on the perpendicular direction of rolling direction.
Saw blade through the overtesting non-cracking indicates that with (O) saw blade that the fracture possibility is high indicates with (X).Resistance to fracture is to determine by only using the saw blade with good tension performance to carry out slice test.
Each material of the No.1-No.15 of the embodiment of the invention demonstrates 1520N/mm
2(155kgf/mm
2) or higher 1.0% initial stress, 196N/mm
2(20kgf/mm
2) or the anisotropy of lower 1.0% initial stress is poor, 4.6mm or bigger Erichsen number and 166,600N/mm
2(17,000kgf/mm
2) or higher Young's modulus.
Internal diameter saw blade with the above-mentioned materials manufacturing has good tension performance, does not all rupture in tension stage and section stage.These materials of the present invention have stable quality of materials, and have minimum difference between highest hardness in the saw blade plane and the minimum hardness.On the other hand, contrast material No.16-No.29 is very poor in some mechanical properties, with the internal diameter saw blade of these material manufacturings of applying or in the tension stage or in the section stage fracture has taken place all.
In above-mentioned Comparative Examples, No.16 material every time draft during temper rolling is very low, and the Erichsen number of this material is little, certainly will rupture in the tension phase.
Draft height during the No.17 material surface dress rolling, the anisotropy difference of this material 1.0% initial stress is big, and it has fracture tendency during straining.
Draft during the No.18 material surface dress rolling is low, and the martensite quantity of this material is few, and this can cause very low Young's modulus and 1.0% very low initial stress, also can rupture during cutting into slices.
Draft during the No.19 material surface dress rolling is low, and 1.0% initial stress of this material is very low, is easy to rupture during cutting into slices.
Draft height during the No.20 material surface dress rolling, this material is rich in martensite, but Erichsen number is very little, is easy to rupture during straining.
The No.21 material has experienced three times cold rolling (comprising finish rolling) circulation, so the anisotropy difference of 1.0% initial stress becomes greatly, this material is easy to rupture during cutting into slices.
The No.22 material has carried out subzero treatment during low-temperature heat treatment, so the timeliness of this material is not enough.As a result, 1.0% initial stress of this material is very low, and is easy to rupture during cutting into slices.
The No.23 material has carried out pyroprocessing during low-temperature heat treatment, thus this material production a large amount of reverse conversion austenite phases, this can reduce Young's modulus and 1.0% initial stress widely.The anisotropy difference of 1.0% initial stress of this material is also very big, is easy to rupture during straining.
The No.24 material during final annealing at H
2Handle in the low atmosphere of concentration.So its surface is gone up and produced deposition, this can cause very low punching test merit load, is easy to rupture during straining.
The No.25 material contains a large amount of Al
2O
3With the inclusion of a large amount of thickness above 5 μ m, the No.26 material contains a large amount of SiO
2With the inclusion of a large amount of thickness above 5 μ m.As a result, the punching test merit load of two kinds of materials has all descended, and ruptures during straining.
The No.27 material contains many sulfide inclusions, so the punching test merit load of this material is very low, and ruptures during straining.
The SiO of No.28 and No.29 material
2Content is high and contain the inclusion that thickness surpasses 5 μ m, so their punching test merit load is very low, and ruptures during straining.
Table 1
(weight %)
| Classification | Steel | C | Si | Mn | P | S | Cr | Ni | N | Solubility Al | O | Cu | SiO 2-MnO-Al 2O 3The composition of foreign material | ||
| SiO 2 | MnO | Al 2O 3 | |||||||||||||
| Embodiment | A | 0.100 | 0.64 | 1.02 | 0.030 | 0.0010 | 16.8 | 6.85 | 0.030 | 0.0008 | 0.0048 | 0.28 | 41 | 43 | l6 |
| B | 0.032 | 0.48 | 1.10 | 0.029 | 0.0008 | 15.8 | 5.12 | 0.190 | 0.0010 | 0.0033 | 0.31 | 34 | 48 | 17 | |
| C | 0.130 | 1.85 | 0.89 | 0.024 | 0.0022 | 15.9 | 6.09 | 0.036 | 0.0009 | 0.0037 | 0.35 | 36 | 49 | 15 | |
| D | 0.178 | 0.21 | 0.49 | 0.028 | 0.0018 | 16.2 | 6.45 | 0.048 | 0.0009 | 0.0039 | 0.21 | 40 | 47 | 13 | |
| E | 0.101 | 0.55 | 1.80 | 0.036 | 0.0007 | 18.5 | 5.90 | 0.102 | 0.0007 | 0.0050 | 0.32 | 48 | 38 | 14 | |
| F | 0.110 | 0.76 | 0.77 | 0.027 | 0.0011 | 13.9 | 8.80 | 0.012 | 0.0011 | 0.0032 | 0.12 | 39 | 46 | 15 | |
| G | 0.096 | 0.60 | 0.95 | 0.014 | 0.0050 | 16.7 | 6.52 | 0.027 | 0.0023 | 0.0090 | 0.30 | 42 | 34 | 24 | |
| H | 0.091 | 0.61 | 0.98 | 0.008 | 0.0034 | 16.8 | 6.73 | 0.025 | 0.0006 | 0.0120 | 0.23 | 55 | 27 | 18 | |
| Comparative Examples | I | 0.098 | 0.61 | 1.00 | 0.035 | 0.0047 | 16.8 | 6.92 | 0.054 | 0.003l | 0.0018 | 0.34 | 35 | 20 | 45 |
| J | 0.108 | 0.65 | 0.96 | 0.029 | 0.0044 | 16.8 | 7.08 | 0.027 | 0.0004 | 0.0132 | 0.32 | 60 | 30 | 10 | |
| K | 0.107 | 0.58 | 0.94 | 0.03l | 0.0096 | 16.7 | 6.78 | 0.066 | 0.0008 | 0.0048 | 0.36 | 47 | 38 | 15 | |
| L | 0.077 | 2.70 | 0.25 | 0.024 | 0.0039 | 14.8 | 5.81 | 0.076 | 0.0010 | 0.0079 | 2.01 | 80 | 10 | 10 | |
| M | 0.067 | 2.95 | 1.02 | 0.024 | 0.0050 | 14.9 | 5.80 | 0.068 | 0.00ll | 0.0082 | 1.96 | 75 | 12 | 13 | |
Table 2
*Thermal treatment means low-temperature heat treatment
| Classification | Material number | Grade of steel | Cold rolling draft (%) | Annealing conditions | Heat-treat condition * | ||||||||
| For the first time cold rolling | For the second time cold rolling | Cold rolling for the third time | Temper rolling (the 4th time) | Temper rolling/passage | Atmosphere/H 2％ | Annealing temperature (℃) | Atmosphere/H 2％ | Temperature (℃) * time (t) | |||||
| Middle | Finally | Middle | Finally | ||||||||||
| Real example | 1 | A | 43 | 38 | 38 | 70 | 8.8 | 95 | 95 | 1000 | 1050 | 95 | 400×2 |
| 2 | A | 38 | 38 | 59 | 62 | 7.8 | 99 | 99 | 1000 | 1050 | 99 | 400×2 | |
| 3 | A | 40 | 34 | 39 | 75 | 15.0 | 95 | 95 | 1000 | 1050 | 95 | 400×2 | |
| 4 | A | 32 | 32 | 58 | 69 | 9.9 | 95 | 75 | 1000 | 1050 | 95 | 400×2 | |
| 5 | A | 44 | 40 | 40 | 70 | 10.0 | 95 | 90 | 1000 | 1050 | 95 | 300×300 | |
| 6 | A | 42 | 42 | 41 | 70 | 11.7 | 95 | 90 | 1000 | 1050 | 99 | 400×300 | |
| 7 | A | 44 | 40 | 40 | 70 | 10.0 | 99 | 95 | 1025 | 1045 | 75 | 600×1 | |
| 8 | B | 18 | 38 | 38 | 75 | 8.3 | 75 | 99 | 960 | 960 | 99 | 400×30 | |
| 9 | C | 38 | 38 | 52 | 67 | 13.4 | 90 | 95 | 1080 | 1000 | 95 | 400×30 | |
| 10 | D | 38 | 38 | 52 | 67 | 11.2 | 99 | 99 | 1140 | 1140 | 95 | 400×30 | |
| 11 | E | 48 | 38 | 38 | 70 | 5.0 | 95 | 95 | 1025 | 1045 | 95 | 400×2 | |
| 12 | F | 44 | 40 | 40 | 70 | 10.0 | 95 | 95 | 1025 | 1045 | 95 | 400×2 | |
| 13 | G | 44 | 40 | 40 | 70 | 7.0 | 95 | 95 | 1025 | 1045 | 95 | 400×2 | |
| 14 | H | 44 | 40 | 40 | 70 | 7.0 | 95 | 95 | 1025 | 1045 | 95 | 400×2 | |
| 15 | A | 44 | 40 | 40 | 70 | 3.5 | 95 | 95 | 1050 | 1050 | 95 | 400×30 | |
Table 3
*Thermal treatment means low-temperature heat treatment
| Classification | Material number | Grade of steel | Cold rolling draft (%) | Annealing conditions | Heat-treat condition * | ||||||||
| For the first time cold rolling | For the second time cold rolling | Cold rolling for the third time | Temper rolling (the 4th time) | Temper rolling/passage | Atmosphere/H 2％ | Annealing temperature (℃) | Atmosphere/H 2％ | Temperature (℃) * time (t) | |||||
| Middle | Finally | Middle | Finally | ||||||||||
| Embodiment | 16 | A | 44 | 40 | 40 | 70 | 2.9 | 90 | 90 | 1000 | 1025 | 95 | 400×30 |
| 17 | A | 44 | 40 | 40 | 70 | 17.5 | 90 | 90 | 1000 | 1025 | 95 | 400×30 | |
| 18 | A | 46 | 46 | 59 | 50 | 7.1 | 90 | 95 | 1000 | 1025 | 95 | 400×30 | |
| 19 | A | 44 | 44 | 55 | 57 | 8.1 | 90 | 75 | 1000 | 1025 | 95 | 400×30 | |
| 20 | A | 30 | 30 | 32 | 85 | 12.1 | 95 | 90 | 1000 | 1025 | 95 | 400×30 | |
| 21 | A | 60 | 50 | - | 70 | 10.0 | 95 | 90 | 1000 | 1025 | 99 | 400×30 | |
| 22 | A | 48 | 38 | 38 | 70 | 8.8 | 95 | 90 | 1000 | 1025 | 99 | 250×300 | |
| 23 | A | 44 | 40 | 40 | 70 | 10.0 | 95 | 90 | 1000 | 1025 | 99 | 650×30 | |
| 24 | A | 44 | 40 | 40 | 70 | 10.0 | 90 | 90 | 1000 | 1050 | 68 | 400×30 | |
| 25 | I | 44 | 40 | 40 | 70 | 10.0 | 90 | 95 | 1000 | 1050 | 95 | 400×30 | |
| 26 | J | 44 | 40 | 40 | 70 | 10.0 | 90 | 95 | 1000 | 1050 | 95 | 400×30 | |
| 27 | K | 44 | 40 | 40 | 70 | 10.0 | 90 | 95 | 1000 | 1050 | 95 | 400×30 | |
| 28 | L | 48 | 38 | 38 | 70 | 11.7 | 90 | 95 | 1050 | 1080 | 90 | 500×60 | |
| 29 | M | 48 | 38 | 38 | 70 | 11.7 | 90 | 95 | 1050 | 1080 | 75 | 500×60 | |
Table 4
| Classification | Material No. | Martensite quantity (% | Plane difference of hardness (Hv) | Young's modulus (GPa) | Initial stress (N/mm 2) | Erichsen number (mm) | Resistance to fracture | |||
| 0.8％ | 1.0％ | Anisotropy is poor | During the tension | During the | ||||||
| Embodiment | ||||||||||
| 1 | 61 | 12 | 185 | 1432 | 1687 | 10 | 5.8 | ○ | ○ | |
| 2 | 53 | 8 | 177 | 1373 | 1589 | 8 | 6.2 | ○ | ○ | |
| 3 | 82 | 16 | 201 | 1530 | 1873 | 14 | 5.5 | ○ | ○ | |
| 4 | 62 | 11 | 186 | 1442 | 1716 | 12 | 5.7 | ○ | ○ | |
| 5 | 61 | 15 | 179 | 1383 | 1618 | 9 | 5.7 | ○ | ○ | |
| 6 | 62 | 10 | 184 | 1432 | 1706 | 9 | 5.8 | ○ | ○ | |
| 7 | 59 | 7 | 182 | 1422 | 1696 | 12 | 5.5 | ○ | ○ | |
| 8 | 80 | 12 | 179 | 1373 | 1638 | 15 | 4.7 | ○ | ○ | |
| 9 | 54 | 16 | 201 | 1549 | 1873 | 13 | 5.6 | ○ | ○ | |
| 10 | 61 | 18 | 207 | 1589 | 1922 | 11 | 4.8 | ○ | ○ | |
| 11 | 76 | 14 | 190 | 1500 | 1775 | 6 | 5.5 | ○ | ○ | |
| 12 | 46 | 19 | 173 | 1353 | 1579 | 15 | 5.0 | ○ | ○ | |
| 13 | 58 | 10 | 180 | 1422 | 1677 | 7 | 5.0 | ○ | ○ | |
| 14 | 63 | 12 | 186 | 1451 | 1736 | 9 | 6.5 | ○ | ○ | |
| 15 | 81 | 17 | 212 | 1618 | 1971 | 5 | 5.0 | ○ | ○ | |
Table 5
| Classification | Material No. | Martensite quantity (%) | Plane difference of hardness (Hv) | Young's modulus (GPa) | Initial stress (N/mm 2) | Erichsen number (mm) | Break fragility | |||
| 0.8％ | 1.0％ | Anisotropy is poor | During the tension | During the section | ||||||
| Comparative Examples | 16 | 71 | 22 | 196 | 1481 | 1736 | 16 | 4.2 | × | Do not detect |
| 17 | 48 | 25 | 181 | 1402 | 1657 | 22 | 4.5 | × | Do not detect | |
| 18 | 38 | 31 | 161 | 1216 | 1441 | 3 | 6.6 | ○ | × | |
| 19 | 47 | 26 | 170 | 1275 | 1510 | 4 | 6.3 | ○ | × | |
| 20 | 91 | 30 | 211 | 1608 | Immeasurability | Immeasurability | 3.3 | × | Do not detect | |
| 21 | 59 | 18 | 183 | 1510 | 1353 | 23 | 4.9 | ○ | × | |
| 22 | 61 | 21 | 173 | 1412 | 1687 | 10 | 5.7 | ○ | × | |
Table 6
| Classification | Material No. | Martensite quantity (%) | Plane difference of hardness (Hv) | Young's modulus (GPa) | Initial stress (N/mm 2) | Erichsen number (mm) | Resistance to fracture | |||
| 0.8％ | 1.0％ | Anisotropy is poor | During the tension | During the section | ||||||
| Comparative Examples | 23 | 37 | 37 | 160 | 1206 | 1412 | 21 | 6.2 | × | Do not detect |
| 24 | 59 | 24 | 182 | 1412 | 1687 | 15 | 4.5 | × | Do not detect | |
| 25 | 59 | 16 | 183 | 1402 | 1677 | 13 | 4.1 | × | Do not detect | |
| 26 | 60 | 17 | 186 | 1422 | 1667 | 12 | 3.8 | × | Do not detect | |
| 27 | 61 | 9 | 183 | 1402 | 1677 | 11 | 3.6 | × | Do not detect | |
| 28 | 62 | 48 | 175 | 1372 | 1638 | 5 | 4.5 | × | Do not detect | |
| 29 | 62 | 56 | 178 | 1343 | 1608 | 9 | 4.4 | × | Do not detect | |
Claims (14)
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5326173A JPH07150306A (en) | 1993-11-30 | 1993-11-30 | Stainless steel thin sheet for id blade base plate excellent in breaking resistance and manufacture thereof |
| JP326173/93 | 1993-11-30 | ||
| JP5326172A JPH07150305A (en) | 1993-11-30 | 1993-11-30 | Stainless steel thin sheet for id blade base plate excellent in breaking resistance and manufacture thereof |
| JP326172/93 | 1993-11-30 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1103437A CN1103437A (en) | 1995-06-07 |
| CN1039724C true CN1039724C (en) | 1998-09-09 |
Family
ID=26572093
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN94102539A Expired - Fee Related CN1039724C (en) | 1993-11-30 | 1994-03-01 | Stainless steel sheet and method for producing thereof |
| CN94102540A Pending CN1103436A (en) | 1993-11-30 | 1994-03-01 | Stainless steel sheet and method for producing thereof |
Family Applications After (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN94102540A Pending CN1103436A (en) | 1993-11-30 | 1994-03-01 | Stainless steel sheet and method for producing thereof |
Country Status (3)
| Country | Link |
|---|---|
| KR (2) | KR970009092B1 (en) |
| CN (2) | CN1039724C (en) |
| DE (2) | DE4406052A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102639742B (en) * | 2009-11-18 | 2016-03-30 | 新日铁住金株式会社 | Austenite stainless steel plate and manufacture method thereof |
| JP5853281B2 (en) * | 2011-03-25 | 2016-02-09 | 日新製鋼株式会社 | Austenitic stainless steel sheet with excellent surface gloss |
| JP6095619B2 (en) * | 2014-08-19 | 2017-03-15 | 日新製鋼株式会社 | Austenitic stainless steel sheet and metal gasket |
| DE102015102255A1 (en) | 2015-02-17 | 2016-08-18 | Sandvik Materials Technology Deutschland Gmbh | Method for producing a strand of stainless steel and strand of stainless steel |
| US11091818B2 (en) | 2015-12-23 | 2021-08-17 | Posco | High strength cold-rolled steel sheet and hot-dip galvanized steel sheet having excellent hole expansion, ductility and surface treatment properties, and method for manufacturing same |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4849166A (en) * | 1985-06-24 | 1989-07-18 | Nisshin Steel Company, Ltd. | High strength stainless steel |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62238333A (en) * | 1986-04-08 | 1987-10-19 | Nippon Steel Corp | Manufacture of ultrathin austenitic stainless steel sheet for water slicer |
| JPH0826404B2 (en) * | 1987-06-22 | 1996-03-13 | 日新製鋼株式会社 | Method for producing high strength stainless steel with excellent overhang strength and toughness |
-
1994
- 1994-02-24 DE DE4406052A patent/DE4406052A1/en not_active Ceased
- 1994-02-24 DE DE4406040A patent/DE4406040A1/en not_active Ceased
- 1994-03-01 CN CN94102539A patent/CN1039724C/en not_active Expired - Fee Related
- 1994-03-01 CN CN94102540A patent/CN1103436A/en active Pending
- 1994-03-04 KR KR1019940004247A patent/KR970009092B1/en not_active IP Right Cessation
- 1994-03-04 KR KR1019940004246A patent/KR970009091B1/en not_active IP Right Cessation
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4849166A (en) * | 1985-06-24 | 1989-07-18 | Nisshin Steel Company, Ltd. | High strength stainless steel |
Also Published As
| Publication number | Publication date |
|---|---|
| KR970009091B1 (en) | 1997-06-05 |
| KR950014346A (en) | 1995-06-16 |
| CN1103437A (en) | 1995-06-07 |
| CN1103436A (en) | 1995-06-07 |
| KR970009092B1 (en) | 1997-06-05 |
| DE4406040A1 (en) | 1995-06-01 |
| KR950014347A (en) | 1995-06-16 |
| DE4406052A1 (en) | 1995-06-01 |
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