CN101363103A - Ni-reduced austenite stainless steel - Google Patents
Ni-reduced austenite stainless steel Download PDFInfo
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- CN101363103A CN101363103A CNA2008101456478A CN200810145647A CN101363103A CN 101363103 A CN101363103 A CN 101363103A CN A2008101456478 A CNA2008101456478 A CN A2008101456478A CN 200810145647 A CN200810145647 A CN 200810145647A CN 101363103 A CN101363103 A CN 101363103A
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- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
Abstract
The invention provides a Ni-reduced austenite stainless steel having excellent recyclability with no problem of producibility depression to be caused by the surface property thereof and having good workability, season cracking resistance, corrosion resistance and stress corrosion cracking resistance in point of the material characteristics thereof. The steel comprises C in an amount of more than 0.05 % (by mass) and within a range of from 0.15 to 0.3 % as (C+N), Si in an amount of at most 1 %, Mn in an amount of from 0.5 to 2.5 %, Ni in an amount of from 3 to 6 %, Cr in an amount of from more than 16 to 25 % and Cu in an amount of from 0.8 to 4 %, and has Md30 of the following formula (1) of from -50 to 10 and SFE of the following formula (2) of at least 5: Md30 = 551-462(C+N)-9.2Si-8.1Mn-29(Ni+Cu)-13.7Cr (1), SFE = 2.2Ni+6Cu-1.1Cr-13Si-1.2Mn+32 (2).
Description
Technical field
The present invention relates to and to suppress for necessary MIN content, not damage surface texture and processibility, anti-natural cracking, corrosion stability and the good austenite stainless steel of anti-stress-corrosion crack the necessary Ni of austenite stainless steel.
Background technology
The austenite stainless steel that with SUS304 is representative is widely used in relating to many-sides such as western-style food utensil and pot, kitchen tackle, building materials, household electrical appliances because of its good processibility and corrosion stability.In addition, not only require processibility, corrosion stability mostly in these purposes, and require appearance design, the distinctive nickeline look of stainless steel internally, outside aspect also is indispensable as the mechanicals starting material.
But, because recently the Ni cost of material goes up, to such an extent as to can see everywhere containing and can not be used for some purposes owing to its cost than the SUS301 of more than 6% Ni and the SUS304 etc. that contains the Ni more than 8%.Must be therewith corresponding, providing in recent years based on 200 be that the steel (patent documentation 1～6) of stainless steel is stainless substitute material as what is called 300.They contain the instead austenite former of Ni of a large amount of (more than 3 quality %) Mn, to seek to save Ni content.In addition, the example (patent documentation 7,8) that does not contain so much Mn and seek to save Ni is also arranged.
Patent documentation 1: special fair 2-29048 communique
Patent documentation 2: the spy opens flat 6-271995 communique
Patent documentation 3: the spy opens the 2006-219751 communique
Patent documentation 4: the spy opens the 2006-219743 communique
Patent documentation 5: the spy opens the 2006-111932 communique
Patent documentation 6: special fair 6-86645 communique
Patent documentation 7: special public clear 60-33186 communique
Patent documentation 8: the spy opens the 2005-154890 communique
Summary of the invention
When making Mn content and surpassing the high Mn austenite stainless steel of 2.5 quality %, when its steel-making, refining, generate deleterious Mn oxide fine particle, must take some countermeasures sometimes from the viewpoint of environment protection.In addition, when stainless steel is utilized again, always so long as non magnetic, be that steel scrap is handled all just as 300, but because the steel that contains high Mn also is non magnetic, contains the many steel scraps of Mn less and be difficult to difference and come, may cause the confusion in steel scrap market so contain the many high price steel scraps of Ni and contain Ni.In addition, because Mn content height, surface quality descends, the painted fault when load increase when causing annealing and pickling easily and clean annealing.At this moment, though Ni has reduced, because of productivity reduces, its effect offsets in resulting cost.
On the other hand, in the technology of the low Ni steel of the such inhibition Mn of patent documentation 7,8, its result has sacrificed as 300 being each of corrosion stability, processibility of stainless good speciality, to seek the reduction of cost.Specifically, the steel of patent documentation 7 austenite when deep-draw processing etc. is too unstable mutually, is easy to generate aging crack after the processing.Therefore can not obtain sufficient degree of finish.The steel of patent documentation 8 is low unfavorable aspect the corrosion stability because of Cr content, in addition, if as can be seen according to the inventor's research, because of solid solution C, N few obtain aspect the sufficient ductility also unfavorable.
The invention provides the Ni that has both good processibility, anti-natural cracking, corrosion stability, anti-stress-corrosion crack in a kind of usability again problem, raw material characteristics aspect good, that the productivity of surface quality of not resulting from reduces and reduce the austenite stainless steel of type.
Above-mentioned problem is reached by processibility, corrosion stability, anti-stress-corrosion crack, the good Ni reduced austenite stainless steel of surface texture, and this austenite stainless steel has following composition: C in quality %: surpass 0.05% and also satisfy that scope, the Si:1% of following (3) formula is following, Mn:0.5～2.5%, Ni:3～6%, Cr: surpass below 16～25%, Cu:0.8～4%, N: the scope, the rest part that satisfy following (3) formula are Fe and unavoidable impurities; Is more than 5 with the austenite stability index Md30 of following (1) formula definition for-50～10, with the stacking fault energy index S FE of following (2) formula definition.
Md30＝551-462(C+N)-9.2Si-8.1Mn-29(Ni+Cu)-13.7Cr (1)
SFE＝2.2Ni+6Cu-1.1Cr-13Si-1.2Mn+32 (2)
0.15≦C+N≦0.3 (3)
Here, the value of the constituent content of representing with quality % in element mark place's substitution of above-mentioned (1)～(3) formula separately.
The invention effect
According to the present invention, can provide the austenite stainless steel of type that Mn content is suppressed at below the 2.5 quality %, usability is good more simultaneously, the productivity of surface quality of not resulting from reduces problem, the Ni that has both good corrosion stability, processibility, anti-stress-corrosion crack are reduced.It is that stainless substitute material is applicable to various uses that this steel can be used as 300.Therefore, the present invention be aspect cost and the quality aspect can with the corresponding invention of the price increase of Ni raw material.
Embodiment
The inventor finishes above-mentioned problem and is carrying out research with keen determination aspect the austenite stainless steel that Ni content is suppressed at below 6%, until obtaining following opinion.
[processibility, plasticity]
As everyone knows, in austenite stainless steel,, thereby strain is disperseed, obtain uniform strain, so-called phase change induction plasticity (TRIP) phenomenon takes place because because of the processing strain, martensite (α ') phase is brought out in the austenite processing that changes hard into of meeting.If as can be seen according to the inventor's research, in the steel of the present invention that reduces Ni content, particularly generate α ' phase time, intervened the ductile that causes by TRIP significantly as C, the N content of the solution strengthening element of left and right sides α ' phase intensity and improved by the processing strain.That is to say, as the Md30 value of (1) formula of the index of austenite stability more than-50, C content than 0.05 quality % many and also (C+N) content when 0.15 quality % is above, will appropriateness generates and have the α ' phase that ductility is improved effectively appropriate intensity.
[anti-natural cracking]
Always known, be the delayed fracture phenomenon that austenite stainless steel is processed the back in deep-draw, placement can be called aging crack in the time of several hours to several days under the atmosphere at room temperature environment of representative with SUS304.In the austenite stainless steel that reduces Ni, also can see same phenomenon., the inventor finds, if by the defined Md30 value of (1) formula below 10, can not suppress aging crack significantly with regard to can excessively not generating α ' phase.
[corrosion stability]
Pitting attack current potential as an evaluation index of corrosion stability generally exists with ... Cr content.If just merely improve the pitting attack current potential, as long as the lower limit of the Cr content in the Ni reduced austenite stainless steel is established height.But, must guarantee good processibility and anti-natural cracking in the present invention, after averaging out with other alloying constituent, as described later, the undergage of Cr content is decided to be 16 quality %.
[anti-stress-corrosion crack]
In austenite stainless steel, add the Ministry of worker and the stress corrosion cracking problem appears in weld part mostly at it.The contriver has studied the method for the various Ni of giving reduced austenite stainless steel anti-stress-corrosion cracks.It found that the behavior of stress corrosion cracking exists with ... stacking fault energy.And detailed experiments found that, when by the stacking fault difficulty index S FE value of (2) formula definition 5 when above, become in the processing mode of problem in stress corrosion cracking, can suppress the generation of stacking fault and possess good anti-stress-corrosion crack.
[surface quality]
Stainless steel requires appearance design in multiple use except corrosion stability and processibility.Therefore, the surface that requirement can efficient be made homogeneous well, and then it plays a big part for the reduction of manufacturing cost.After successive atmosphere annealing, carry out continuous pickling, on accurately machined AP (annealing and pickling) service line, the homogeneity of the oxide skin that generates during annealing, also have the separability that causes by pickling of this oxide skin all to become the important factor of decision manufacturing as 2D.The contriver finds, in the steel below Ni is reduced to 6 quality %, Mn content is defined in 2.5 quality % when following, uses and can be with SUS304 the same the removing of oxide skin of implementing well on the AP service line of always SUS304 identical operations condition.Thus, can avoid being accompanied by the rising of the manufacturing cost that Mn content increases.
Mn content surpasses the occasion of 2.5 quality %, and the load of pickling increases, and is difficult to reduce cost.Can think as described below about the mechanism that the load in this pickling increases.In the common austenite stainless steel that with SUS304 is representative, the Cr oxide compound generates at the surface of steel plate homogeneous during annealing, can efficient carry out pickling well.But, be reduced to the occasion that Mn content in the steel below 6% surpasses 2.5 quality % at Ni, generate the Cr oxide compound when annealing in the atmosphere, generate simultaneously the Cr-Mn composite oxides easily unevenly, between the position of position that generates the Cr oxide compound and generation Cr-Mn composite oxides, in pickling, produce different.That is to say, the pickling inequality occurs.Under such situation, in order to obtain good pickled surface, the pickling of longer time must be arranged, the load of pickling increases, and then causes productivity to reduce.The result of all research needs only Mn content below 2.5 quality % as can be seen, just can avoid this problem.
In addition, Mn content increases and also becomes the essential factor that productivity reduces in clean annealing.That is to say that when annealing, it is painted to generate blue xanchromatic easily under with the reducing atmosphere of hydrogen as main body.Can think as described below about this point.Usually, along with Mn content uprises, the ratio that the Mn on the surface of steel plate occupies increases.Because Mn is in the easy oxidation of annealed temperature range internal ratio Cr, thus when reductive action is relatively lower in the gas atmosphere of clean annealing when higher (dew point than), generate the Mn oxide film at surface of steel plate easily, in most cases, with blue yellow painted.Mn content can avoid resulting from the painted of such Mn oxide film when 2.5 quality % are following, can production efficiency not provide the surface quality equal with SUS304 with not reducing.
Below, the alloying constituent that contains in the steel of the present invention is described.
[alloying constituent]
C, N bring out the mutually useful element of martensite (α ') for solution strengthening processing.When α ' generates mutually in steel of the present invention, manifest for making the sufficient ductility that is caused by TRIP, making the total content (hereinafter referred to as " (C+N) content ") of C and N is more than the 0.15 quality %.In addition, obtain significant ductility raising effect, guarantee that the content that C surpasses 0.05 quality % is important for stable.C, when N content is too much, can excessive hardization, become the major reason that hinders processibility.Therefore preferably (C+N) content is defined as below the 0.3 quality %.About C, N content separately, adjust in the preferred scope of C below 0.15 quality %, more preferably in the scope below 0.1 quality %.N is defined as below the 0.25 quality %, but usually as long as adjust in the scope about 0.04～0.2 quality %.
Mn is more cheap than Ni, is the useful austenite former that replaces the function of Ni.In the present invention, in order to make full use of its function, must guarantee the Mn content that 0.5 quality % is above.On the other hand, when Mn content is superfluous, the problem of the environment protection in the steel making working procedure takes place easily.In addition, become the major reason that the productivity that causes resulting from surface texture reduces (aforementioned).Therefore, Mn content is limited in below the 2.5 quality %, is preferably limited to be lower than 2.5 quality %.
Ni is the necessary element of austenite stainless steel, but in the present invention, from the viewpoint that reduces cost, carries out the composition design of lowland inhibition Ni content as far as possible.Specifically, Ni content is reduced to below the 6 quality %.Also can be set at and be lower than 6 quality %.But,, must guarantee the Ni content that 3 quality % are above in order in above-mentioned Mn content range, to realize having both the one-tenth balance-dividing of manufacturing, processibility, corrosion stability.
Cr is the film formed necessary element of passivation that guarantees the stainless steel corrosion stability.Cr content can not fully guarantee to become the desired corrosion stability of existing austenite stainless steel that the present invention replaces object sometimes when 16 quality % are following.But, because Cr is ferrite former, excessively adds Cr and cause generating in a large number mutually at the high-temperature area delta ferrite, become the major reason of infringement hot workability and not good.The result of all research can contain the Cr of 25 quality % at the most in the present invention.Therefore, the content of Cr is defined as and surpasses 16～25 quality %.
Si is the element useful to deoxidation in the steel-making, but Si content for a long time, and the steel hardization becomes the major reason of damaging processibility.In addition, because Si is a ferrite former, superfluous interpolation can cause generating the infringement hot workability mutually in a large number at the delta ferrite of high-temperature area.Therefore, Si content is limited in below the 1 quality %.
Cu be suppress to result from processing bring out work hardening that martensitic phase generates, to the softening element that works of austenite stainless steel.In addition, because Cu is an austenite former, so corresponding with the increase of Cu content, the setting degree of freedom of Ni content enlarges, and the composition design that suppresses Ni becomes easy.In addition, Cu improves the very effective element in SFE value aspect, by suppressing the generation of stacking fault, plays a part big to improving anti-stress-corrosion crack.In order fully to obtain such effect, must guarantee the Cu content that 0.8 quality % is above.But, contain a large amount of Cu that surpasses 4 quality %, damage hot workability easily.Therefore, Cu content is defined as 0.8～4 quality %.
P and S sneak into as unavoidable impurities, but allow P as many as 0.045 quality % substantially, allow S as many as 0.03 quality %.
Steel of the present invention can be founded by general stainless steel making working procedure.According to the manufacture method of general austenite stainless steel steel plate can make for example cold rolled annealed steel plate of thickness of slab 0.1～3.5mm thereafter.
(embodiment 1)
Found shown in the table 1 austenite stainless steel of forming, obtain continuous casting steel billet after, under 1230 ℃ of extrusion temperatures, make the hot rolled strip of thickness of slab 3mm by hot rolling.After 1 minute annealing of hot rolled strip 1100 ℃ * soaking of enforcement, by the cold rolling cold-rolled steel strip of making thickness of slab 1mm, implement 1 minute annealing of 1050 ℃ * soaking, pickling, make the annealing and pickling steel band.
Table 1
Underscore: specialized range of the present invention is outer)
※1：Md30＝551-462(C+N)-9.2Si-8.1Mn-29(Ni+Cu)-13.7Cr
※2：SFE＝2.2Ni-1.1Cr-13Si-1.2Mn+6Cu+32
By the Md30 value is that approximately-50～-40 steel C, F, G and Md30 value are that-13.7 steel 0 cuts out JIS 13B test film respectively, implements the tension test of the direction parallel with respect to rolling direction.Gauge length is taken as 50mm, and draw speed is taken as 40mm/min, measures the gauge length that post-rift test film is connected, and obtains breaking elongation.In order to use as the replacement that is not the Ni existing general austenite stainless steel steel plate of reducing type, its breaking elongation of austenite stainless steel steel plate annealing material of wishing this thickness of slab is the good processibility more than 40%.It the results are shown in table 2.
Table 2
| Distinguish | Steel No. | C (quality %) | C+N (quality %) | Md30 | Breaking elongation (%) |
| Example of the present invention | C | 0.051 | 0.174 | -48.4 | 51 |
| Comparative example | F | 0.051 | 0.146 | -38.4 | 35 |
| Example of the present invention | G | 0.052 | 0.151 | -44.6 | 40 |
| Comparative example | 0 | 0.035 | 0.186 | -13.7 | 38 |
Underscore: outside the specialized range of the present invention
As table 2 shows, C content surpass 0.05 quality % and also (C+N) the of the present invention steel of content more than 0.15 quality % show high breaking elongation more than 40%.Relative therewith, (C+N) to be lower than the breaking elongation of steel F of 0.15 quality % low be 35% to content.In addition, C content is low to be the steel 0 of less than 0.05 quality %, although (C+N) content is more than 0.15 quality %, but can not realize the breaking elongation more than 40%.
(embodiment 2)
Use the annealing and pickling steel band of the steel A～E, the M that make by embodiment 1 to cut out the discoideus blank that in the scope of external diameter φ 76～84mm, has every the various degree external diameters of 2mm, with the deep-drawing test machine enforcement cup-shaped deep-draw processing of extending.Use inside diameter D d to be φ 40mm, corner curvature rp drift as former and the profile Dp of 4mm, coating viscosity 60mm on blank and surface that former contacts as 3mm as φ 43mm, corner curvature rd
2The lubricating oil of/s shapes blank to deep-draw and extends under the condition of 5 tons of pressure-pad-forces.
Molding placed 24 hours in atmosphere at room temperature after, judge that there is flawless in molding cup edge, obtains the natural cracking limit deep-draw ratio of each steel with following (4) formula.
[aging crack limit deep-draw ratio]=Db
Max/ Dp (4)
Here, Db
MaxBe that maximum blank diameter (mm), the Dp that natural cracking do not take place is formpiston external diameter (mm).In order to use, wish this natural cracking limit deep-draw than being good anti-natural cracking more than 2.0 as the replacement that is not the Ni existing general austenite stainless steel steel plate of reducing type.It the results are shown in table 3.
Table 3
| Distinguish | Steel No. | C+N (quality %) | Md30 | Aging crack limit deep-draw ratio |
| Example of the present invention | A | 0.161 | -6.6 | ≧2.1 |
| Example of the present invention | B | 0.452 | -29.3 | ≧2.1 |
| Example of the present invention | C | 0.174 | -48.4 | ≧2.1 |
| Example of the present invention | D | 0.152 | 9.8 | 2.05 |
| Comparative example | E | 0.155 | 16.1 | 1.80 |
| Comparative example | M | 0.162 | 16.9 | 1.60 |
Underscore: outside the specialized range of the present invention
As shown in table 3 like that, the Md30 value can realize the deep-draw of the natural cracking limit than being good anti-natural cracking more than 2.0 at the steel below 10.
(embodiment 3)
Steel B, the H that makes by embodiment 1 as standard test with JIS G0577, the pitting attack current potential of I.Experimental liquid is the 3.5%NaCl aqueous solution, and temperature is 30 ℃, with sweep velocity 0.33mV/sec current potential is risen with voltage stabilizer from spontaneous potential, to become 100mA/cm at the passive area corrosion current
2Above current potential (the relative SCE of mV) is as the pitting attack current potential.In order to use, wish that this pitting attack current potential is the above corrosion stability of 200mV as the replacement that is not the Ni existing general austenite stainless steel steel plate of reducing type.It the results are shown in table 4.
Table 4
| Distinguish | Steel No. | Cr (quality %) | C+N (quality %) | Md30 | Pitting attack current potential (the relative SCE of mV) |
| Example of the present invention | B | 17.93 | 0.152 | -29.3 | 235 |
| Comparative example | H | 15.82 | 0.159 | -24.1 | 185 |
| Example of the present invention | I | 16.03 | 0.156 | -22.9 | 201 |
Underscore: outside the specialized range of the present invention
As shown in table 4 such, the steel that contains the above Cr of 16 quality % can obtain good pitting attack current potential.
(embodiment 4)
From the steel B, the J that make by embodiment 1, K, N, cut out the blank of external diameter φ 80mm, make deep-draw drawing cup with the deep-drawing test mechanism of formpiston diameter phi 40mm.With accurate stapling machine the cup edge is counted at the bottom of the cup and to be cut off, supply with 42% magnesium chloride boiling test with JIS G0576 regulation in the position of height 15mm.In order to use, even hope is through the anti-stress-corrosion crack of crackle did not take place more than 24 hours yet in this boiling is tested as the replacement that is not the Ni existing general austenite stainless steel steel plate of reducing type.It the results are shown in table 5.
Table 5
| Distinguish | Steel No. | SFE | Crackle time of origin (h) |
| Example of the present invention | B | 33.4 | 120 |
| Example of the present invention | J | 6.3 | 36 |
| Comparative example | K | 4.2 | 20 |
| Comparative example | N | 4.8 | 22 |
Underscore: outside the specialized range of the present invention
As shown in table 5 like that, even the SFE value at the steel of the example of the present invention more than 5 through crackle did not take place more than 24 hours yet, show good anti-stress-corrosion crack.
(embodiment 5)
From the cold-rolled steel sheet (steel band of annealing last stage) of the steel B, the C that make by embodiment 1, I, J, L, take the square cutting plate of 50mm, carry out the annealing experiment under air atmosphere in the laboratory.In being set at 1100 ℃ atmosphere annealing furnace, make each sample heating after 60 seconds, promptly be clipped in and carry out chilling between water-cooled copper plate.Be immersed in the nitration mixture aqueous solution of nitric acid of hydrofluoric acid 60 ℃, 2 quality % and 10 quality %, measure and remove descaling until the time that becomes homogeneous surfaces (being called " pickling time " here).It the results are shown in table 6.
Table 6
| Distinguish | Steel No. | Mn (quality %) | The pickling time (sec) |
| Example of the present invention | B | 1.62 | 22 |
| Example of the present invention | C | 1.98 | 23 |
| Example of the present invention | I | 1.91 | 25 |
| Example of the present invention | J | 1.98 | 28 |
| Comparative example | L | 2.53 | 65 |
Underscore: outside the specialized range of the present invention
As shown in table 6 such, the of the present invention steel pickling time of Mn content below 2.5 quality % does not particularly follow special service line speed to reduce on general continuous annealing pickling line below 30 seconds, is judged as and can implements good pickling.
(embodiment 6)
Similarly to Example 5, take the square cutting plate of 50mm, in the laboratory, carry out the clean annealing experiment here from the cold-rolled steel sheet of steel B, C, I, J, L.Carry out following experiment: in supplying with continuously the silica tube of hydrogen that dew point is adjusted at 100% in-40 ℃～-60 ℃ scopes, keep sample, this silica tube integral body packed in 1100 ℃ the process furnace into heating after 60 seconds, promptly silica tube integral body is taken out in the stove put cold.By the surface of the cooled sample of visual observation, estimating has non-coloring.Obtain about each steel and not produce painted upper limit dew point (being called " dew point ceiling temperature " here).In order to use as the replacement that is not the Ni existing general austenite stainless steel steel plate of reducing type, wishing to have in this clean annealing test dew point ceiling temperature becomes good coloring resistance more than-50 ℃.It the results are shown in table 7.
Table 7
| Distinguish | Steel No. | Mn (quality %) | The dew point ceiling temperature (℃) |
| Example of the present invention | B | 1.62 | -40 |
| Example of the present invention | C | 1.98 | -40 |
| Example of the present invention | I | 1.91 | -43 |
| Example of the present invention | J | 1.98 | -45 |
| Comparative example | L | 2.53 | -60 |
Underscore: outside the specialized range of the present invention
As shown in table 7 such, the steel of of the present invention example of Mn content below 2.5 quality % has its dew point ceiling temperature fully aware of at the coloring resistance more than-50 ℃, can avoid the reduction of the productivity in the clean annealing.
Claims (1)
1. Ni reduced austenite stainless steel, its processibility, anti-natural cracking, corrosion stability, anti-stress-corrosion crack, surface texture are good, be characterised in that to have following composition: C in quality %: surpass 0.05% and also satisfy that scope, the Si:1% of following (3) formula is following, Mn:0.5～2.5%, Ni:3～6%, Cr: surpass below 16～25%, Cu:0.8～4%, N: the scope, the rest part that satisfy following (3) formula are Fe and unavoidable impurities; Is more than 5 with the austenite stability index Md30 of following (1) formula definition for-50～10, with the stacking fault energy index S FE of following (2) formula definition,
Md30＝551-462(C+N)-9.2Si-8.1Mn-29(Ni+Cu)-13.7Cr (1)
SFE＝2.2Ni+6Cu-1.1Cr-13Si-1.2Mn+32 (2)
15≦C+N≦0.3 (3)。
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| Application Number | Priority Date | Filing Date | Title |
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| JP2007207482 | 2007-08-09 | ||
| JP2007207482A JP5014915B2 (en) | 2007-08-09 | 2007-08-09 | Ni-saving austenitic stainless steel |
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| CN101363103A true CN101363103A (en) | 2009-02-11 |
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| US (1) | US20090041613A1 (en) |
| EP (1) | EP2025770A1 (en) |
| JP (1) | JP5014915B2 (en) |
| KR (1) | KR20090015817A (en) |
| CN (1) | CN101363103A (en) |
| TW (1) | TWI394847B (en) |
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| CN102301028A (en) * | 2009-01-30 | 2011-12-28 | 山特维克知识产权股份有限公司 | Stainless austenitic low ni steel alloy |
| CN104975237A (en) * | 2011-06-16 | 2015-10-14 | 新日铁住金不锈钢株式会社 | Ferritic stainless-steel sheet with excellent non-ridging property and process for producing same |
| CN105518161A (en) * | 2013-07-05 | 2016-04-20 | 奥托库姆普联合股份公司 | Stainless steel resistant to delayed cracking and a method for its production |
| CN107075651A (en) * | 2014-09-17 | 2017-08-18 | 新日铁住金株式会社 | Austenite stainless steel steel plate |
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| JP5349015B2 (en) * | 2008-11-19 | 2013-11-20 | 日新製鋼株式会社 | Method for producing Ni-saving austenitic stainless hot-rolled steel sheet, slab and hot-rolled steel sheet |
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-
2008
- 2008-07-25 KR KR1020080073032A patent/KR20090015817A/en not_active Application Discontinuation
- 2008-08-01 TW TW097129188A patent/TWI394847B/en active
- 2008-08-05 US US12/222,201 patent/US20090041613A1/en not_active Abandoned
- 2008-08-06 EP EP08014087A patent/EP2025770A1/en not_active Withdrawn
- 2008-08-07 CN CNA2008101456478A patent/CN101363103A/en active Pending
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102301028A (en) * | 2009-01-30 | 2011-12-28 | 山特维克知识产权股份有限公司 | Stainless austenitic low ni steel alloy |
| US8540933B2 (en) | 2009-01-30 | 2013-09-24 | Sandvik Intellectual Property Ab | Stainless austenitic low Ni steel alloy |
| CN102301028B (en) * | 2009-01-30 | 2014-12-31 | 山特维克知识产权股份有限公司 | Stainless austenitic low ni steel alloy |
| CN104975237A (en) * | 2011-06-16 | 2015-10-14 | 新日铁住金不锈钢株式会社 | Ferritic stainless-steel sheet with excellent non-ridging property and process for producing same |
| CN104975237B (en) * | 2011-06-16 | 2017-06-23 | 新日铁住金不锈钢株式会社 | The excellent ferrite series stainless steel plate of wrinkle resistance and its manufacture method |
| CN105518161A (en) * | 2013-07-05 | 2016-04-20 | 奥托库姆普联合股份公司 | Stainless steel resistant to delayed cracking and a method for its production |
| CN107075651A (en) * | 2014-09-17 | 2017-08-18 | 新日铁住金株式会社 | Austenite stainless steel steel plate |
| CN107075651B (en) * | 2014-09-17 | 2019-02-05 | 新日铁住金株式会社 | Austenite stainless steel steel plate |
Also Published As
| Publication number | Publication date |
|---|---|
| TWI394847B (en) | 2013-05-01 |
| EP2025770A1 (en) | 2009-02-18 |
| JP5014915B2 (en) | 2012-08-29 |
| JP2009041072A (en) | 2009-02-26 |
| TW200923106A (en) | 2009-06-01 |
| KR20090015817A (en) | 2009-02-12 |
| US20090041613A1 (en) | 2009-02-12 |
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