CN109837470A - A kind of nitrogenous economical austenitic stainless steel of high intensity and its manufacturing method - Google Patents
A kind of nitrogenous economical austenitic stainless steel of high intensity and its manufacturing method Download PDFInfo
- Publication number
- CN109837470A CN109837470A CN201711225914.8A CN201711225914A CN109837470A CN 109837470 A CN109837470 A CN 109837470A CN 201711225914 A CN201711225914 A CN 201711225914A CN 109837470 A CN109837470 A CN 109837470A
- Authority
- CN
- China
- Prior art keywords
- stainless steel
- nitrogenous
- austenitic stainless
- high intensity
- economical
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
Abstract
A kind of nitrogenous economical austenitic stainless steel of high intensity and its manufacturing method, the steel chemical composition weight percent are as follows: C:0.05~0.15%, Si:0.3~1%, Mn:8.5~11.0%, Cr:14.0~16.0%, Ni:1.0~2.5%, N:0.10~0.25%, P < 0.08%, S < 0.01%, Cu:0.5~2.0%, Mo:0.1~0.5%, remaining is Fe and inevitable impurity, and Md30/50≥20℃.The present invention is in the fabrication process, pass through cold rolling twice+flexibility annealing, crystal grain is refined using the generation and inversion of strain-induced martensite, the final size that obtains is in 500nm crystal grain below, to greatly improve the intensity of material, specific performance is as follows: yield strength >=650MPa, tensile strength >=1000MPa, elongation percentage >=35% is suitble to prepare high-intensitive thin gauge accurate band steel.
Description
Technical field
The present invention relates to a kind of nitrogenous economical austenitic stainless steel of high intensity and its manufacturing methods, relate more specifically to one
Kind nitrogenous economical austenitic of high intensity as obtained from thermo-mechanical deformation repeatedly+flexibility annealing acquisition nanometer-size die is stainless
Steel and its manufacturing method.
Background technique
With the progress of industrial technology, requirement of all trades and professions to metal material is continuously improved, and low cost, high intensity will be
The development trend of the following metal material.Such as the lightweight demand for development in fields such as automobile, aviations, it is necessary to which material has more
High intensity and better plasticity, while cost cannot be too high.In addition, being also needed a large amount of high-strength in precise electronic industry
Strip is spent, the requirement that electronic product size increasingly reduces is met.
Stainless steel is the important selection of industrial circle material due to having both certain intensity and corrosion resistance.But tradition
Austenitic stainless steel 304,316 low strength, the requirement of high-strength material cannot be met very well, moreover, these products contain
There is higher nickel content, cost is relatively high.In addition, the price fluctuation of these products is also big since Ni price fluctuation is big, ratio is brought
Biggish economic risk.Therefore, if a kind of economical stainless steel can be developed, and it is high-strength by technological means to meet material
The requirement of degree will have a very important significance to realize the purpose of low-cost high-strength.
In fact, in recent years, people utilize N alloying means, the section nickel even austenitic stainless steel without nickel is obtained, greatly
It reduces costs greatly, and improves intensity to a certain extent, these products fields such as electrical article, container of being in have obtained extensively
Application.But the N content for the nickel-saving type austenitic stainless steel developed at present is usually 0.2% hereinafter, yield strength is only
400MPa or so, tensile strength are only capable of reaching 700~800MPa, and intensity can't fully meet the requirement of high-strength stainless steel.
If improving nitrogen content to 0.4% or more, preparing high nitrogen stainless steel can achieve the requirement of high-strength stainless steel, such as surrender is by force
Degree reaches 600MPa or more, and tensile strength reaches 1000MPa or more.But high nitrogen steel actual industrial production process difficulty very
Greatly, the high nitrogen steel board of wide cut can't be prepared at present.Therefore, current to achieve the purpose that high intensity, it is all made of skin-pass
Method, that is, usually said hard state stainless steel improves the strength of materials using the generation of strain-induced martensite, and 301 series are hard
State stainless steel is typical example.
Although skin-pass has obtained preferable application in terms of producing high-strength stainless steel, production thin gauge or
On Ultra-thin strip, since quenched drafts is difficult accurately to control, it is uneven often to encounter strength control, and band steel plate type is difficult to
The problem of control, the presence of these problems make to produce high quality high-strength stainless steel strip difficulties.
Chinese patent CN200810042817.X is by adding higher Mn content, it is ensured that the stability of austenite structure,
To keep nonmagnetic energy under the conditions of obtaining cold deformation.Contain the N of high level, under the conditions of cold deformation, material in the patent
Intensity can greatly increase, obtain high-intensity performance.But the patent obtains high intensity and is still through cold-rolling deformation, this and tradition
It is quenched the same, be faced with the problems such as same plate performance difference is big, and template is difficult to control accurately.
Chinese patent CN201310367890.5 discloses a kind of high-nitrogen austenitic stainless steel, and N content is greater than 1.0%.
In fact, under industrial mass production mode, it at present can't product of the steady production N content higher than 1.0%.Therefore, high
The production of nitrogen steel also lies substantially in laboratory or pilot scale stage, size are restricted.
Summary of the invention
The object of the present invention is to provide a kind of nitrogenous economical austenitic stainless steel of high intensity and its manufacturing method, the steel
In metallographic structure crystallite dimension in 500nm hereinafter, its yield strength >=650MPa, tensile strength >=1000MPa, elongation percentage >=
35%, it significantly improves Steel material intensity and keeps good plasticity, while having that steel is small with plate performance difference, template is good excellent
Point.
To achieve the above object, the technical scheme is that
A kind of nitrogenous economical austenitic stainless steel of high intensity, chemical component weight percentage are as follows: C:0.05~
0.15%, Si:0.3~1%, Mn:8.5~11.0%, Cr:14.0~16.0%, Ni:1.0~2.5%, N:0.10~
0.25%, P < 0.08%, S < 0.01%, Cu:0.5~2.0%, Mo:0.1~0.5%, remaining is Fe and inevitable impurity,
And above-mentioned element need to meet simultaneously following relationship:
Md30/50>=20 DEG C, Md30/50Calculation formula is as follows:
Md30/50=413-462* (C%+N%) -9.2*Si%-8.1*Mn%-9.5*Ni%-3.7*Cr%-18.5*
Mo%.
Preferably, Mn:9.5~10.5% in the nitrogenous economical austenitic stainless steel of high intensity, with weight percent
Meter.
Preferably, Cr:14~15% in the nitrogenous economical austenitic stainless steel of high intensity, by weight percentage.
Preferably, Ni:1.5~2.0% in the nitrogenous economical austenitic stainless steel of high intensity, with weight percent
Meter.
Preferably, N:0.10~0.20% in the nitrogenous economical austenitic stainless steel of high intensity, with weight percent
Meter.
Preferably, Cu:1.0~1.5% in the nitrogenous economical austenitic stainless steel of high intensity, with weight percent
Meter.
Preferably, Mo:0.1~0.5% in the nitrogenous economical austenitic stainless steel of high intensity, with weight percent
Meter.
Further, the metallographic structure of the nitrogenous economical austenitic stainless steel of high intensity is single austenite structure,
Crystallite dimension≤500nm.
Yield strength >=650MPa of the nitrogenous economical austenitic stainless steel of high intensity, tensile strength >=1000MPa,
Elongation percentage >=35%.
The effect of each element in composition of steel design of the present invention:
C:C is the strong element for being formed, stablizing and expand austenitic area, and C plays weight to formation austenite structure at room temperature
It acts on.But the too high plasticity that can reduce stainless steel of C content, and it is unfavorable to the corrosion resistance of stainless steel, therefore, control of the present invention
C content processed is 0.05~0.15%.
Mn:Mn is weaker austenite former, but is strong austenite structure stable element in stainless steel,
And solubility of the N in steel can be improved.In low nickle type austenitic stainless steel, the elements compoundings such as Mn and C, N in steel are acted on, part
Ni is replaced to ensure that stainless steel is austenite structure at room temperature.But Mn has negative effect to the corrosion resistance of austenitic stainless steel,
Therefore Mn content can not be too high, and it is 8.5~11% that the present invention, which controls Mn content, it is preferred that Mn:9.5~10.5%.
Cr:Cr is most important alloying element in stainless steel, is to obtain stainless steel rustless property and corrosion proof guarantee.This hair
Bright Cr content is controlled 14~16%, and reason that cannot be too high is to obtain austenite structure single at room temperature.This hair
Bright middle Cr content preferred scope is 14~15%.
Mo:Mo be also in stainless steel improve corrosion resistance important element, the present invention in order to improve corrosion resistance, into
Mo microalloying is gone, studies have shown that the coordination of Mo, N element has a significant effect to the corrosion resistance for improving stainless steel.
But Mo is precious metal element, and therefore, the content of steel addition Mo of the present invention is less, is controlled 0.1~0.5%, it is preferred that Mo:0.1
~0.5%.
Ni:Ni be to be formed with the mutually most important element of stable austenite, and the anti-reductic acid of stainless steel can also be enhanced
Ability and raising processing performance, but in order to reduce cost, the present invention substantially reduces the content of Ni, controls 1~2.5%, preferably
, Ni:1.5~2.0%.
N:N is very strongly formation, the element for stablizing and expanding austenitic area in stainless steel.N is removed in stainless steel
It can substitute except precious resource such as Ni, material can also be significantly improved under the premise of significantly reducing material plasticity and toughness
The intensity of material, moreover it is possible to improve rustless property, corrosion resistance and the precipitation for delaying carbide of stainless steel etc..But since N is in stainless steel
In solubility it is limited, in order to avoid rimhole occurs in process of setting in steel, the determination of N content must be with other alloys members
Plain coordinative role ensures stainless steel in room temperature with other alloying element compound actions to ensure that N exists with solid solution condition
It is down single phase austenite tissue.Therefore, it is 0.10~0.25% that the present invention, which controls N content, it is preferred that N:0.10~0.20%.
Cu:Cu can improve stainless steel cold-forming property, and with the raising of Cu content, the flow harden index of stainless steel is bright
Aobvious decline, therefore, the Cu content of steel of the present invention is maintained at higher content, and specific control is 0.5~2.0%, it is preferred that Cu:
1.0~1.5%.
Si:Si is added in low-nickel austenitic stainless steel smelting process as deoxidier, therefore, low in steel in order to control
Always [O] content must have certain reduction Si content in steel.But Si is again ferrite former in stainless steel, in order to
Ensuring stainless steel at room temperature is single phase austenite tissue, and Si content must limit.The present invention control Si content be 0.3~
1.0%.
P:P is considered as harmful element in stainless steel, should try to control more lower better.
S: in view of Mn content is higher in steel of the present invention, MnS field trash easy to form influences corrosion resisting property, therefore it is required that
S content is controlled in lower level.
The manufacturing method of the nitrogenous economical austenitic stainless steel of high intensity of the present invention comprising following steps:
1) it smelts, cast
Pass through electric furnace smelting, converter smelting, external refining according to above-mentioned chemical component, is casting continuously to form base；
2) hot rolling+hot-roll annealing pickling
3) once cold rolling+primary flexible annealing
Once cold rolling drafts 50~80%；Primary 800~950 DEG C of annealing temperature of flexibility, annealing soaking time 1~
3min；
4) secondary cold-rolling+secondary flexible annealing
Secondary cold-rolling drafts 50~80%；Secondary 800~950 DEG C of annealing temperature of flexibility, annealing soaking time 1~
3min。
Further, in step 1), in converter steelmaking process, using Si deoxidation, control reduction Si content is 0.3~1.0%.
In step 1), in external refining process, refining time >=40 minute, soft mixing time >=10 minute of argon gas are gone forward side by side
Row Ca processing.
Also, the metallographic structure of the nitrogenous economical austenitic stainless steel of high intensity is single austenite structure, crystal grain
Size≤500nm.
Yield strength >=650MPa of the nitrogenous economical austenitic stainless steel of high intensity of the present invention, tensile strength >=
1000MPa, elongation percentage >=35%.
The present invention is in process for making:
The present invention is in converter steelmaking process, and using Si deoxidation, control reduction Si content is 0.3~1.0%.It is protected in the present invention
Holding and restoring the content of Si in steel is to reduce the effective measures of total [O] content in steel, and total [O] content is lower in steel, field trash
Content is lower, so as to improve polishing performance.When restoring Si content greater than 0.3%, total [O] content in molten steel can be reduced
To 50ppm hereinafter, the degree of purity of molten steel is guaranteed well.
The present invention guarantees that refining time is no less than 40 minutes, the soft mixing time of argon gas is no less than 10 in external refining process
Minute, and carry out Ca processing.The refining and the soft mixing time of argon gas for guaranteeing enough time, can promote filling for inclusion content in melting steel
Divide and float, improves Molten Steel Cleanliness.For high-melting-point Al that may be present in steel2O3It is mingled with, is handled and be modified by Ca, it can
To reduce influence of the high-melting-point field trash to properties for follow, improve the surface quality of finished product, is conducive to improve corrosion resistance
Energy.
The present invention carries out refinement crystal grain by the way of cold rolling twice+flexibility annealing, and each cold roling reduction is 50~
80%, 800~950 DEG C of flexible annealing temperature, anneal 1~3min of soaking time.Metastable austenite passes through cold rolling in the present invention,
A large amount of strain-induced martensite is formed, is then annealed again, crystal grain can be refined.
The present invention obtains nanoscale crystal grain using cold rolling+flexibility annealing process, improves the strength of materials and keeps higher
Plasticity, cardinal principle are: by cold-rolling deformation, materials microstructure is made to be changed into strain-induced martensite tissue by austenite, due to
Md of the invention30/50Keep higher temperature (Md30/50>=20 DEG C), austenite structure is unstable during cold-rolling deformation, easily
It is changed into martensite, cold rolling finishes, and strain-induced martensite amount (volume fraction) can achieve 80% or more, original austenite group
It knits to have obtained adequately broken.Flexible annealing is then carried out, sufficiently broken tissue is recrystallized, for composition of steel of the present invention
For system, recrystallization temperature can reach in 800~950 DEG C of temperature ranges, and compared to existing annealing temperature (>=1100
DEG C), annealing temperature of the present invention is lower, and tissue is not easy to grow up, to play Grain refinement.It is broken by above-mentioned crystal grain twice
Broken and recrystallization, finally obtains nanoscale crystal grain, according to Hall-Petch formula it is recognised that the intensity of material will obtain greatly
Amplitude improves.
The present invention is obtained excellent resistance under the premise of substantially reducing the cost of raw material by the alloy design of science
Corrosive nature and mechanical performance.In addition, making material obtain the crystal grain of Nano grade by the reasonable flexible annealing process of design
Degree to greatly improve the strength of materials, while also having good plasticity.Moreover, using mechanically deform repeatedly (cold rolling)+flexibility
The processing method of annealing, obtain size in 500nm crystal grain below, it is ensured that the tensile strength of material in 1000MPa or more, and
Have the advantages that strip is small with plate performance difference, template is good, overcomes template in traditional high-intensitive thin gauge steel preparation process
Uncontrollable difficulty.Therefore, the present invention is very suitable to prepare high-intensitive thin gauge accurate band steel.
Beneficial effects of the present invention:
Austenitic stainless steel of the present invention adds a certain number of under the premise of being greatly reduced using noble metal Ni
The elements such as Mn, N, Cu obtain austenite structure single at room temperature, and have excellent cold-forming property.In addition, steel of the present invention
Kind contains higher Cr content, and adds a small amount of Mo element, it is ensured that product has good corrosion resistance.
In the fabrication process, the present invention is annealed by cold rolling twice+flexibility, using the generation and inversion of strain-induced martensite come
Crystal grain is refined, the final size that obtains, to greatly improve the intensity of material, makes the yield strength of steel in 500nm crystal grain below
>=650MPa, tensile strength >=1000MPa, while there is 35% or more elongation percentage.
Steel material of the present invention has high-intensitive, high-ductility, can substitute very well at present by cold rolling it is quenched obtain it is stainless
Steel hard state steel.Meanwhile compared to traditional skin-pass, the flexible method for annealing that the present invention uses, in the system of Ultra-thin product
It is standby it is upper have the advantages that plate shape is good, performance stable and uniform, be the new method of production high-strength stainless steel accurate band steel.
Detailed description of the invention
Fig. 1 is the metallographic structure photo that 1 heat of the embodiment of the present invention moves back steel after pickling.
Fig. 2 is 2 steel Huey test result photo of the embodiment of the present invention.
Fig. 3 is the metallographic structure photo of 3 steel of the embodiment of the present invention.
Specific embodiment
Below with reference to embodiment and attached drawing, the invention will be further described.
Embodiment 1
Composition of steel is as shown in table 1, and the two-step method of electric furnace, AOD is taken to smelt, and smelting process, which controls, restores Si content in molten steel
Greater than 0.3%, live actual analysis is 0.45%.LF station refining time is not less than 40min, and practical is 45min.Argon is soft to be stirred
The time is mixed not less than 10min, practical is 12min.Ca processing, B microalloying are carried out in LF station terminal.Molten steel is obtained by continuous casting
To slab, slab moves back pickling, once cold rolling, primary flexible annealing and pickling, secondary cold-rolling and secondary flexibility using hot rolling, heat and moves back
Fiery pickling and smooth, produces the strip of 2B surface state.Wherein, once cold rolling drafts is 55%, primary flexible annealing temperature
Degree is 850 DEG C, and primary flexibility annealing time is 2min, and secondary cold-rolling drafts is 55%, and secondary flexibility annealing temperature is 850
DEG C, secondary flexible annealing soaking time is 3min.Composition detection shows: strip total oxygen content [O] < 50ppm, and practical is 38ppm.
The field trash grade in steel is evaluated using metallographic method, evaluating basis is GB/T 10561-2005, and the results are shown in Table 2.
The metallographic structure of the present embodiment steel is as shown in Figure 1.
As shown in Table 2, the amount of inclusions in steel of the present invention is few.Therefore, manufacturing process through the invention can obtain
The molten steel of high cleanliness is conducive to the corrosion resistance for improving material.
The measuring mechanical property result of the present embodiment is shown in Table 3.
Fig. 1 is that heat moves back the metallographic structure after pickling.As shown in Figure 1, the metallographic structure of steel of the present invention is single austenite
Tissue, it is seen then that the present invention, by adding the elements such as reasonable Mn, N, obtains under the premise of reducing noble metal Ni constituent content
Single austenite structure at room temperature.
Embodiment 2
Composition of steel is as shown in table 1, takes the two-step method of electric furnace, AOD to smelt, the control requirement and embodiment 1 of smelting process
It is identical, each major control point actual value are as follows: LF refining time 40min, the soft mixing time of Argon are 15min.Molten steel by continuous casting,
Hot rolling, hot-roll annealing pickling, once cold rolling, primary flexible annealing and pickling, secondary cold-rolling, secondary flexible annealing and pickling, smooth, life
The high-intensitive nickel-saving type austenitic stainless steel strip of output 2B surface state, wherein once cold rolling drafts is 60%, primary soft
Property annealing temperature be 800 DEG C, primary flexibility annealing time is 3min, and secondary cold-rolling drafts is 50%, secondary flexible annealing temperature
Degree is 900 DEG C, and secondary flexible annealing soaking time is 3min.The measuring mechanical property result of the present embodiment is shown in Table 3.
The spot corrosion performance test of material, test result are as follows: the weight-loss ratio of material are carried out using GB/T 17897-1999
It (g/m^2*h) is 7.89, therefore, steel of the present invention has preferable resistance to spot corrosion performance.
Fig. 2 is the present embodiment Huey test result.As seen from Figure 2, using cold rolling twice+flexible annealing twice
Technique can be such that the carbide in finished product is dissolved completely, not have intercrystalline corrosion.
Embodiment 3
Composition of steel is as shown in table 1, takes the two-step method of electric furnace, AOD to smelt, the control requirement and embodiment 1 of smelting process
It is identical, each major control point actual value are as follows: the LF refining time is 40min, and the soft mixing time of Argon is 15min.Molten steel is by connecting
Casting, hot rolling, heat move back pickling, once cold rolling, primary flexible annealing and pickling, secondary cold-rolling, secondary flexible annealing and pickling, smooth, life
The high-intensitive nickel-saving type austenitic stainless steel strip of output 2B surface state.Once cold rolling drafts is 60%, and primary flexibility is moved back
Fiery temperature is 850 DEG C, and primary flexibility annealing time is 3min, and secondary cold-rolling drafts is 50%, and secondary flexibility annealing temperature is
900 DEG C, secondary flexibility annealing time is 1.5min.The measuring mechanical property result of the present embodiment is shown in Table 3.
The metallographic structure of the present embodiment is as shown in Figure 3.From the figure 3, it may be seen that crystallite dimension is about 500nm in metallographic structure.It can
See, metastable austenite is formed a large amount of strain-induced martensite, then annealed again, can be refined by cold rolling in the present invention
Crystal grain.And the crystallite dimension of material is controlled in Nano grade, is greatly improved by cold rolling twice and flexible annealing by the present invention
The strength of materials, and good plasticity can be kept.
Embodiment 4
Composition of steel is as shown in table 1, and composition of steel is as shown in table 1, takes the two-step method of electric furnace, AOD to smelt, the control of smelting process
System requires and embodiment 1 is identical, each major control point actual value are as follows: the LF refining time is 40min, and the soft mixing time of Argon is
15min.Molten steel moves back pickling, once cold rolling, primary flexible annealing and pickling, secondary cold-rolling, secondary flexibility by continuous casting, hot rolling, heat
It is annealing and pickling, smooth, produce the high-intensitive nickel-saving type austenitic stainless steel strip of 2B surface state.Once cold rolling drafts is
60%, primary flexibility annealing temperature is 850 DEG C, and primary flexibility annealing time is 1min, and secondary cold-rolling drafts is 60%, secondary
Flexible annealing temperature is 900 DEG C, and secondary flexibility annealing time is 1min.The measuring mechanical property result of the present embodiment is shown in Table 3.
As shown in Table 3, yield strength >=650MPa of steel of the present invention, tensile strength >=1000MPa, elongation percentage >=35%,
As it can be seen that strip prepared by the present invention has very high intensity, and there is good plasticity.
1 unit of table: wt%
| C | Si | S | P | Cr | Mn | Ni | N | Cu | Mo | |
| Embodiment 1 | 0.080 | 0.45 | 0.001 | 0.02 | 14.0 | 8.9 | 1.25 | 0.11 | 1.00 | 0.50 |
| Embodiment 2 | 0.065 | 0.63 | 0.002 | 0.03 | 16.0 | 8.5 | 1.08 | 0.20 | 0.70 | 0.35 |
| Embodiment 3 | 0.030 | 1.00 | 0.002 | 0.03 | 14.8 | 11.0 | 2.40 | 0.22 | 1.58 | 0.10 |
| Embodiment 4 | 0.050 | 0.67 | 0.003 | 0.02 | 15.3 | 10.2 | 1.9 | 0.15 | 1.85 | 0.15 |
Table 2
Table 3
| Yield strength (MPa) | Tensile strength (MPa) | Elongation percentage (%) | |
| Embodiment 1 | 702 | 1105 | 36.9 |
| Embodiment 2 | 680 | 1058 | 39.01 |
| Embodiment 3 | 712 | 1103 | 35.80 |
| Embodiment 4 | 691 | 1005 | 38.47 |
Claims (14)
1. a kind of nitrogenous economical austenitic stainless steel of high intensity, chemical component weight percentage are as follows: C:0.05~0.15%,
Si:0.3~1%, Mn:8.5~11.0%, Cr:14.0~16.0%, Ni:1.0~2.5%, N:0.10~0.25%, P <
0.08%, S < 0.01%, Cu:0.5~2.0%, Mo:0.1~0.5%, remaining is Fe and inevitable impurity, and above-mentioned element
Following relationship need to be met simultaneously:
Md30/50>=20 DEG C, Md30/50Calculation formula is as follows:
Md30/50=413-462* (C%+N%) -9.2*Si%-8.1*Mn%-9.5*Ni%-3.7*Cr%-18.5*Mo%.
2. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1, which is characterized in that the high intensity contains
Mn:9.5~10.5% in nitrogen economical austenitic stainless steel chemical component, by weight percentage.
3. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1 or 2, which is characterized in that described high-strength
Cr:14~15% in nitrogenous economical austenitic stainless steel chemical component is spent, by weight percentage.
4. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1-3, which is characterized in that described
Ni:1.5~2.0% in high-intensitive nitrogenous economical austenitic stainless steel chemical component, by weight percentage.
5. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1-4, which is characterized in that described
N:0.10~0.20% in high-intensitive nitrogenous economical austenitic stainless steel chemical component, by weight percentage.
6. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1-5, which is characterized in that described
Cu:1.0~1.5% in high-intensitive nitrogenous economical austenitic stainless steel chemical component, by weight percentage.
7. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1-6, which is characterized in that described
Mo:0.1~0.5% in high-intensitive nitrogenous economical austenitic stainless steel chemical component, by weight percentage.
8. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1-7, which is characterized in that described
The metallographic structure of high-intensitive nitrogenous economical austenitic stainless steel is single austenite structure, crystallite dimension≤500nm.
9. the nitrogenous economical austenitic stainless steel of high intensity according to claim 1-8, which is characterized in that described
Yield strength >=650MPa of high-intensitive nitrogenous economical austenitic stainless steel, tensile strength >=1000MPa, elongation percentage >=
35%.
10. such as the manufacturing method of the described in any item nitrogenous economical austenitic stainless steels of high intensity of claim 1-9, including such as
Lower step:
1) it smelts, cast
Pass through electric furnace smelting, converter smelting, external refining according to the chemical component of any one of claim 1-7, is casting continuously to form base；
2) hot rolling+hot-roll annealing pickling
3) once cold rolling+primary flexible annealing
Once cold rolling drafts 50~60%；Primary 800~900 DEG C of annealing temperature of flexibility, anneal 1~3min of soaking time；
4) secondary cold-rolling+secondary flexible annealing
Secondary cold-rolling drafts 50~60%；Secondary 800~900 DEG C of annealing temperature of flexibility, anneal 1~3min of soaking time.
11. the manufacturing method of the nitrogenous economical austenitic stainless steel of high intensity according to claim 10, which is characterized in that
In step 1), Si content 0.3~1.0% is controlled using Si deoxidation in converter steelmaking process.
12. the manufacturing method of the nitrogenous economical austenitic stainless steel of high intensity according to claim 10, which is characterized in that
In step 1), in external refining process, refining time >=40 minute, soft mixing time >=10 minute of argon gas, and Ca processing is carried out.
13. the manufacturing method of the described in any item nitrogenous economical austenitic stainless steels of high intensity of 0-12 according to claim 1,
It is characterized in that, the metallographic structure of the nitrogenous economical austenitic stainless steel of high intensity is single austenite structure, crystal grain ruler
Very little≤500nm.
14. the manufacturing method of the described in any item nitrogenous economical austenitic stainless steels of high intensity of 0-13 according to claim 1,
It is characterized in that, yield strength >=650MPa of the nitrogenous economical austenitic stainless steel of high intensity, tensile strength >=
1000MPa, elongation percentage >=35%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711225914.8A CN109837470B (en) | 2017-11-29 | 2017-11-29 | High-strength nitrogen-containing economical austenitic stainless steel and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711225914.8A CN109837470B (en) | 2017-11-29 | 2017-11-29 | High-strength nitrogen-containing economical austenitic stainless steel and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109837470A true CN109837470A (en) | 2019-06-04 |
| CN109837470B CN109837470B (en) | 2022-04-01 |
Family
ID=66882008
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201711225914.8A Active CN109837470B (en) | 2017-11-29 | 2017-11-29 | High-strength nitrogen-containing economical austenitic stainless steel and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109837470B (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111593183A (en) * | 2020-05-11 | 2020-08-28 | 武汉科技大学 | Production method for refining grain size of austenitic stainless steel plate strip |
| CN112853054A (en) * | 2021-01-06 | 2021-05-28 | 北京科技大学 | Preparation method for reducing peeling defect of 200-series economical austenitic stainless steel |
| CN114310035A (en) * | 2022-01-11 | 2022-04-12 | 哈尔滨焊接研究院有限公司 | Flux-cored wire suitable for nickel-saving austenitic stainless steel backing welding and preparation method thereof |
| CN115398022A (en) * | 2020-04-22 | 2022-11-25 | 株式会社Posco | Low-cost austenitic stainless steel having high strength and high formability and method for manufacturing the same |
| CN115466908A (en) * | 2022-09-29 | 2022-12-13 | 浙江青山钢铁有限公司 | Selenium-containing calcium-containing free-cutting stainless steel and preparation method thereof |
| CN116018421A (en) * | 2020-06-23 | 2023-04-25 | 浦项股份有限公司 | High strength austenitic stainless steel having excellent productivity and cost reduction effect and method for producing the same |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52110215A (en) * | 1976-03-13 | 1977-09-16 | Nippon Metal Ind | Deep drawing austenite stainless steel |
| JP2006028542A (en) * | 2004-07-13 | 2006-02-02 | Yamashin Steel Kk | Nonmagnetic austenitic stainless steel and nonmagnetic stainless steel worked material |
| WO2010074710A2 (en) * | 2008-12-16 | 2010-07-01 | L. E. Jones Company | Superaustenitic stainless steel and method of making and use thereof |
| CN101942612A (en) * | 2010-08-09 | 2011-01-12 | 振石集团东方特钢股份有限公司 | Nickel-saving austenitic stainless steel with good corrosion resistance |
| CN101984123A (en) * | 2010-11-08 | 2011-03-09 | 东北大学 | Preparation method of stainless steel coach plate for high-speed train |
| CN102925790A (en) * | 2012-10-31 | 2013-02-13 | 钢铁研究总院 | Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology |
| EP1783240B1 (en) * | 2005-11-03 | 2015-04-08 | Daido Steel Co., Ltd. | High-nitrogen austentic stainless steel |
| CN104878317A (en) * | 2015-04-30 | 2015-09-02 | 振石集团东方特钢有限公司 | Hot-rolling production method for low-nickel austenitic stainless steel coils |
| CN105200340A (en) * | 2015-09-23 | 2015-12-30 | 宝钢不锈钢有限公司 | 800-1,600 MPa grade high strength austenitic stainless steel, manufacturing method and warm forming method |
| CN106834973A (en) * | 2016-12-28 | 2017-06-13 | 宝钢不锈钢有限公司 | A kind of economical high intensity austenitic stainless steel used for rail vehicle and its manufacture method |
-
2017
- 2017-11-29 CN CN201711225914.8A patent/CN109837470B/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52110215A (en) * | 1976-03-13 | 1977-09-16 | Nippon Metal Ind | Deep drawing austenite stainless steel |
| JP2006028542A (en) * | 2004-07-13 | 2006-02-02 | Yamashin Steel Kk | Nonmagnetic austenitic stainless steel and nonmagnetic stainless steel worked material |
| EP1783240B1 (en) * | 2005-11-03 | 2015-04-08 | Daido Steel Co., Ltd. | High-nitrogen austentic stainless steel |
| WO2010074710A2 (en) * | 2008-12-16 | 2010-07-01 | L. E. Jones Company | Superaustenitic stainless steel and method of making and use thereof |
| CN101942612A (en) * | 2010-08-09 | 2011-01-12 | 振石集团东方特钢股份有限公司 | Nickel-saving austenitic stainless steel with good corrosion resistance |
| CN101984123A (en) * | 2010-11-08 | 2011-03-09 | 东北大学 | Preparation method of stainless steel coach plate for high-speed train |
| CN102925790A (en) * | 2012-10-31 | 2013-02-13 | 钢铁研究总院 | Method for producing high-strength and elongation product automobile steel plate by continuous annealing technology |
| CN104878317A (en) * | 2015-04-30 | 2015-09-02 | 振石集团东方特钢有限公司 | Hot-rolling production method for low-nickel austenitic stainless steel coils |
| CN105200340A (en) * | 2015-09-23 | 2015-12-30 | 宝钢不锈钢有限公司 | 800-1,600 MPa grade high strength austenitic stainless steel, manufacturing method and warm forming method |
| CN106834973A (en) * | 2016-12-28 | 2017-06-13 | 宝钢不锈钢有限公司 | A kind of economical high intensity austenitic stainless steel used for rail vehicle and its manufacture method |
Non-Patent Citations (2)
| Title |
|---|
| 许昌淦等: "《合金钢与高温合金》", 28 February 1993, 北京航空航天大学出版社 * |
| 马国财: "高速列车用不锈钢车厢板性能的研究", 《中国优秀硕士学位论文全文数据库工程科技Ⅱ辑》 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115398022A (en) * | 2020-04-22 | 2022-11-25 | 株式会社Posco | Low-cost austenitic stainless steel having high strength and high formability and method for manufacturing the same |
| CN115398022B (en) * | 2020-04-22 | 2023-11-28 | 株式会社Posco | Low cost austenitic stainless steel having high strength and high formability and method of manufacturing the same |
| CN111593183A (en) * | 2020-05-11 | 2020-08-28 | 武汉科技大学 | Production method for refining grain size of austenitic stainless steel plate strip |
| CN116018421A (en) * | 2020-06-23 | 2023-04-25 | 浦项股份有限公司 | High strength austenitic stainless steel having excellent productivity and cost reduction effect and method for producing the same |
| CN112853054A (en) * | 2021-01-06 | 2021-05-28 | 北京科技大学 | Preparation method for reducing peeling defect of 200-series economical austenitic stainless steel |
| CN114310035A (en) * | 2022-01-11 | 2022-04-12 | 哈尔滨焊接研究院有限公司 | Flux-cored wire suitable for nickel-saving austenitic stainless steel backing welding and preparation method thereof |
| CN115466908A (en) * | 2022-09-29 | 2022-12-13 | 浙江青山钢铁有限公司 | Selenium-containing calcium-containing free-cutting stainless steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN109837470B (en) | 2022-04-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109837470A (en) | A kind of nitrogenous economical austenitic stainless steel of high intensity and its manufacturing method | |
| CN109207846A (en) | A kind of high anti-corrosion section nickel high-nitrogen austenitic stainless steel | |
| CN111575588B (en) | Martensite precipitation hardening stainless steel and preparation method and application thereof | |
| CN109504900B (en) | Ultrahigh-strength cold-rolled phase-change induced plasticity steel and preparation method thereof | |
| CN110218852B (en) | 301 stainless steel production method, 301 stainless steel and application | |
| CN110029274A (en) | A kind of 1600MPa grades of High-strength high-plasticity drop stamping steel and preparation method thereof | |
| CN115141984B (en) | High-entropy austenitic stainless steel and preparation method thereof | |
| CN104195458B (en) | A kind of stainless steel hot-rolling plate of low relative permeability and preparation method thereof | |
| CN109423577B (en) | High-strength multi-phase steel tinning raw plate and manufacturing method thereof | |
| CN112501493B (en) | Nickel-saving high-nitrogen austenitic stainless steel with excellent pitting corrosion resistance and sulfuric acid corrosion resistance and manufacturing method thereof | |
| CN102560286A (en) | Non-magnetic hard-section nickel austenitic stainless steel and preparation method thereof | |
| CN107988550A (en) | Steel for pressurized water reactor nuclear power station pressure vessel support and manufacturing method thereof | |
| CN109112431B (en) | Nonmagnetic stainless steel cold-rolled sheet for deep drawing forming and preparation method thereof | |
| CN114592155B (en) | High-surface-quality 430 ferrite stainless steel BA plate and manufacturing method thereof | |
| CN113355601B (en) | Low-cost high-corrosion-resistant steel bar and production method thereof | |
| CN109609729B (en) | Stainless steel plate with 650 MPa-grade yield strength and manufacturing method thereof | |
| CN110499453A (en) | The high-strength two-sided stainless steel clad plate of one kind and its manufacturing method | |
| CN104513933A (en) | Inexpensive non-magnetic stainless steel and manufacturing method thereof | |
| CN105112782A (en) | Low-temperature ferrite LT-FH40 steel plate applied to hot-rolled ships and production method thereof | |
| CN110819893A (en) | Austenitic stainless steel for electronic products and preparation method thereof | |
| CN109852885A (en) | A kind of two phase stainless steel and preparation method thereof | |
| CN109913763A (en) | The good inexpensive cold-rolled biphase steel of 1000MPa grades of cold-forming properties and its manufacturing method | |
| CN109628828A (en) | A kind of low yield strength ratio super thick water power high-strength steel sheet and its manufacturing method | |
| CN109072387A (en) | The excellent superhigh intensity high-extension steel plate of yield ratio and its manufacturing method | |
| CN106834931B (en) | A kind of hot die steel of thermal fatigue resistance and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| TA01 | Transfer of patent application right | ||
| TA01 | Transfer of patent application right |
Effective date of registration: 20190822 Address after: The Hong Kong Industrial Zone in Luoyuan Bay Development Zone of Luoyuan County of Fuzhou City, Fujian province 350600 Applicant after: Baosteel Desheng Stainless Steel Co., Ltd. Address before: 580 Baoshan District Changjiang Road, Shanghai, No. 200431 Applicant before: Baosteel Stainless Steel Co.,Ltd. |
|
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |