CN102400064A - Austenitic stainless steel with stamping performance and manufacturing method thereof - Google Patents
Austenitic stainless steel with stamping performance and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to an austenitic stainless steel which comprises the following chemical components in percentage by weight: less than or equal to 0.03% of C, less than or equal to 0.75% of Si, 2.0-3.5% of Mn, 16-19% of Cr, 8.0-9.50% of Ni, 2.0-3.0% of Cu, 0.1-0.25% of Nb, less than or equal to 0.03% of N, less than or equal to 0.005% of Al and the balance of Fe and inevitable impurities, wherein the contents of Nb, C and N meets the conditions that Nb-8(C+N)>=0 and (C+Nb)<=0.30%. The invention also relates to a manufacturing method of the austenitic stainless steel. The manufacturing method comprises the following steps: in a smelting process, controlling the slag basicity at 1.5-2.5, deoxidizing by utilizing ferrosilicon or silicomanganese with the aluminum content being less than 1.0wt% under a vacuum or non-vacuum condition, and casting to obtain a steel ingot or steel billet by utilizing fully killed molten steel under a non-oxidation protection condition; performing hot rolling and cold rolling; and in a thermal treatment process of a material subjected to cold rolling, rapidly cooling at the temperature of 1010-1070 DEG C, thus ensuring to obtain a metallographic structure finer than the level of 6.0. The austenitic stainless steel has the characteristics of being excellent in stamping performance, avoiding cracking caused by stamping and avoiding intermediate annealing.
Description
Technical field
The present invention relates to a kind of austenitic stainless steel, particularly a kind of punching performance is good, avoid stamping cracking, avoid the austenitic stainless steel and the method for manufacture thereof of process annealing.
Background technology
Austenitic stainless steel has better comprehensive mechanical property; Be convenient to carry out mechanical workout, punching press and welding; And in oxidative environment, have superior corrosion resistance can and good heat-resistant; Thereby be widely used in various manufacture fields, particularly have the advantage that other stainless steel hardly matches especially in the deep-draw field.
But the stainless-steel cold-rolling product is at some goods of industries such as galley equipment and apparatus, thermos cup (kettle), sun power, precise electronic; Because deep processing performance, surface quality, mechanical property and process annealing etc. are had relatively high expectations, common 304 generally can not satisfy processing request.Domestic and international for this reason sophisticated stainless steel enterprise has all carried out targetedly to its material that is used for stamping products that the composition design and processes improves, and guarantees that its product can satisfy user's use.Improve its deep drawability such as CN1113661A through the Cu content that in 304 stainless steels, adds below 3%; US5571343 is through adding Cu in 304 stainless steels, the Md30 of control material and ferrite content improve the stamping cracking problem of material; JP2001081535A adds Si and Al content on 304 bases, reach to reduce the purpose that Md30 improves forming property; JP07204791A improves the deep drawability of material through the relation between elements such as control C, N, Ni; CN1502716A also is that the ferrite content through composition adjustment material reaches the purpose of improving forming property; CN1364944A forms the deep processing performance that improves its material through the inclusion of control material, and what it was more paid close attention to is that material processing method is to Effect on Performance.
Control device by above-mentioned patented material sees that the overwhelming majority is on 304 stainless bases, adds elements such as Ni, Cu, Al or Mn, and the Md30 that reduces material reaches the purpose of improving plasticity.But still can not satisfy the requirement of punching performance.
Summary of the invention
The object of the present invention is to provide a kind of punching performance good, avoid stamping cracking, avoid the austenitic stainless steel of punching press process annealing.
Be the realization above-mentioned purpose, austenitic stainless steel of the present invention, the weight percent proportioning of its chemical ingredients is: C≤0.03%, Si≤0.75%; Mn:2.0-3.0%, Cr:16-19%, Ni:8.0-9.50%, Cu:2.0-3.0%; Nb:0.1-0.25%, N≤0.03%, Al≤0.005%; The content of Nb, C, N must satisfy simultaneously: Nb-8 (C+N)>=0, (C+Nb)≤0.30%, all the other are Fe and unavoidable impurities.
The present invention is on 304 stainless steel bases; Except that adding Cu, Mn element reduction Md30, also reduce by 304 stainless C, N content, add the Nb element; Reduce the negative impact of material intermediate gap atom pairs material forming performance to greatest extent, thereby realize improving the purpose of material forming performance.
Another object of the present invention is to provide the method for manufacture of above-mentioned austenitic stainless steel.This method comprises:
In smelting process, basicity of slag is controlled at 1.5-2.5, under vacuum or non-vacuum condition, adopts aluminium content to be lower than 1.0% ferrosilicon or silicomanganese deoxidation, under the non-oxidation protective condition, pours into steel ingot or steel billet through abundant sedative molten steel;
The hot rolling heating and temperature control that the present invention is fit to is at 1200-1240 ℃; The present invention compares cold rolling hardenability with SUS304 little, passage maximum distortion rate can near or equal 35%, thereby under same deformation rate condition, can reduce the cold rolling passage;
Material heat treatment process 1010-1070 after cold rolling ℃ fast cold, like water-cooled or air-cooled, to guarantee to obtain 6.0 grades of more tiny metallographic structures of ratio.
Above-mentioned technology can be produced on metallurgical works is produced the equipment of SUS304.
Description of drawings
Fig. 1 is that the Control and Inclusion Removal effect of the embodiment of the invention 1 steel and 18Cr-8Ni-0.009Al steel compares.Wherein, 1a is the inclusion pattern of 18Cr-8Ni-0.009Al steel; 1b is the inclusion pattern of steel of the present invention.
Fig. 2 is that the cold hardening of the embodiment of the invention 1 steel and SUS304 steel is compared.
Embodiment
Below the present invention is carried out comparatively detailed explanation.
Unless otherwise, content all refers to weight percent content among the present invention.
SUS304 belongs to metastable austenitic stainless steel; In the cold deformation process, this metastable austenite can change strain-induced martensite into, because the generation of strain-induced martensite makes material have very high intensity and hardness; Thereby cause the difficulty of material redeformation; Influence the deep draw performance of material, can cause material to ftracture when serious, perhaps distortion back timeliness cracking in deformation process.Md30 (℃) be one of the important indicator (formula 1) that characterizes this martensitic transformation degree, Md30 (℃) the strain-induced martensite amount that forms during low more material cold deformation is few more, the punching performance of material is good more, timeliness rimose tendency is low more after the material punching press.
Md30(℃)＝551-462(C％+N％)-9.2Si％-8.1Mn％-13.7Cr％
-18.5Mo％-29(Ni％+Cu％)-68Nb％-1.42(γ-8.0)(1)
γ in the formula: material grains degree
The inventor finds the austenitic stainless steel punching course, and essence is the flow process of metal between mould, and this process is accompanied by the distortion of materials sclerosis, thereby influences forming property.Strain hardening is that the passage that the accumulation of dislocation has hindered other dislocation causes; The burying in oblivion of dislocation, arrange again and cross slip will reduce the hardenability of distortion; The stacking fault energy of metal is than higher simultaneously; Metal flow is easier or distortion is easier, thereby increases the shaping of the element advantageous material that improves the metal stacking fault energy.
C: carbon is strong stable austenite and expansion austenitic area element in stainless steel, also is the material reinforcement element.But because atoms such as the relative metal Fe of C atomic radius, Cr, Ni, Cu are much smaller, in metallic substance, belong to interstitial atom, be unfavorable for the corrosion resistance nature and the punching performance of material.Therefore, carbon content of the present invention be defined as≤0.03%.Preferably, C≤0.02%, more preferably 0.007-0.02%.
Si: silicon is a kind of deoxidant element commonly used in the stainless steel smelting process, must guarantee to have in the molten steel Si of certain content, and deoxidation of molten steel could be fully; Silicon reduces the stacking fault energy of material on the other hand, is unfavorable for distortion of materials.Thereby the scope of silicone content confirmed as≤0.75%.Preferably, silicone content is 0.20-0.70%, more preferably 0.40-0.70.
Mn: manganese is one of austenite former; Effect with stable austenite tissue; Simultaneously manganese still be a kind of cheapness, reduce Md30 (℃) element (formula 1), but consider that it has certain negative interaction to material corrosion resistance, the manganese content in the steel is confirmed as: 2.0-3.5%.Preferably, manganese content is 2.5-3.5%, more preferably 2.7-3.45%.
Cr: chromium is the most basic stainless element, is the fundamental element that stainless steel obtains erosion resistance.Simultaneously Cr also is the ferrite former in the stainless steel, because the present invention requires lower C, N (strong austenite former) content, for the balance of the phase that keeps material, chromium content of the present invention is 16-19%.Be preferably 16.1-18.8%, more preferably 16.5-18.6%.
Ni:Ni belongs to strong austenite formation, stable element, and higher stacking fault energy is arranged, and is the main alloy that improves the material forming performance, but because its its heavy addition of expensive price limit, nickel content of the present invention is 8.0-9.0%.Be preferably 8.05-9.0%, more preferably 8.06-8.7%.
Cu:Cu belongs to austenite formation, stable element, and higher stacking fault energy is arranged, and is the main alloy that improves the material forming performance, but the hot workability of too high Cu content influence material, nickel content of the present invention is 2.0-3.0%.Be preferably 2.05-2.95%, more preferably 2.08-2.92% most preferably is 2.3-2.92%.
N: nitrogen is the intensive austenite former, because N belongs to the forming property that interstitial element is unfavorable for material, the nitrogen content of steel of the present invention is≤0.03%.Be preferably≤0.02%, 0.005-0.015% more preferably.
C in Nb:Nb and the stainless steel, N have very strong bonding force; Reduced the deleterious effect of the C in the austenitic stainless steel, N interstitial atom, made material " IF " change, the Nb refinement crystal grain of austenitic stainless steel; The Md30 of reduction material (℃); The stacking fault energy of the Nb increase material of solid solution helps the interflow of material, but too high Nb improves intensity, the increase production cost of material, thereby Nb content 0.1-0.25% of the present invention.For guaranteeing to add the effect of Nb, the content of Nb, C, N must satisfy: Nb-8 (C+N)>=0 reaches (C+Nb)≤0.30%.Be preferably 0.15-0.25%.
Al:Al in stainless steel mainly with Al
2O
3The form of inclusion exists, because such is mingled with and belongs to and can not be mingled with the fragility of flow of metal, the forming property of material is had bigger harm, for limiting its damaging effect regulation Al of the present invention≤0.005%, is preferably 0.003-0.005%.
P: phosphorus is harmful element in stainless steel, should make in the steel phosphorus content low as far as possible, but the stainless steel smelting dephosphorization does not also have economy, effective means, and steel of the present invention confirms that the content of phosphorus is≤0.03%.
S: sulphur also is harmful element in stainless steel, in steel, generates MnS etc. easily and is mingled with, and sulphur worsens the hot workability of steel simultaneously, and the corrosion resistance nature of material is also had negative effect.Thereby the present invention is≤0.02% with sulphur content in the steel, be preferably≤0.005%.
The present invention is through reducing the stainless interstitial atom C of SUS304, N content; Improve the distortion of materials flowing property; Increase the forming property that Cu content improves material; Improve the Md30 that Mn, Cu element reduce material (℃), the Md30 that add harm that Nb alleviates C, N interstitial atom, reduces material (℃), the crystal grain of refinement material gains in strength and avoids the material stamping cracking, makes forming property of the present invention be improved.
Grain fineness number after the material heat treatment, not only influence Md30 (℃) (formula 1), and can improve the intensity of material to a certain extent, reduce the risk of stamping cracking.
When austenitic stainless steel is used as stamping material; It in most cases all is the material that adopts thin specification; Thereby the punch process material not only has the higher requirement of ratio to the forming property of material; Level to the inclusion that influences the material punch process also has higher requirement simultaneously, thereby the present invention has stipulated the production technique of this material simultaneously.
ME with good punching performance austenitic stainless steel of the present invention: in smelting process; Basicity of slag is controlled at 1.5-2.5; Under vacuum or non-vacuum condition; Adopt aluminium content to be lower than 1.0% ferrosilicon or silicomanganese deoxidation, under the non-oxidation protective condition, pour into steel ingot or steel billet through abundant sedative molten steel, the hot rolling heating and temperature control that the present invention is fit to is at 1200-1240 ℃; The present invention compares cold rolling hardenability with SUS304 little, and pass deformation rate can be near 35%, thereby under same deformation rate condition, can reduce the cold rolling passage; 1010-1070 ℃ of this material heat treatment process in cold rolling back is fast cold, to guarantee to obtain 6.0 grades of more tiny metallographic structures of ratio.This material can be produced the equipment production of SUS304 at metallurgical works.
Below in conjunction with embodiment the present invention is further specified.
Table 1 for the typical composition (%) of material typical composition of the present invention (%) and related patent U.S. Patent No., Md30 (℃) comparison.Visible by table 1; Except that the JP08295980A that improves the bulging ability, the Md30 of most of patented product (℃) all be lower than conventional SUS304, all obtained the target of improving material drawing performance; But Md30 of the present invention (℃) controlled to-47 ℃; Be minimum in the different materials, under identical texturizing condition, the ability that this material continues cold deformation is stronger relatively.
Table 1 patented material typical composition, Md30 (℃) contrast
Chemical ingredients that table 2 the present invention implements to be listed as and Md30 (℃) the control result
Table 2 listed material of the present invention implement the Composition Control of row and calculate gained Md30 (℃), visible variation along with composition, Md30 (℃)-20 ℃～-75 ℃ range, all be lower than the about 15 ℃ level of conventional SUS304.
Test Example 1: mechanical property
Carry out tension test according to GB/T 228-2002 method, measure the steel of the embodiment of the invention and ys, tensile strength, yield tensile ratio, the unit elongation of SUS304 steel, its result sees table 3.
Test Example 2: according to GB/T 4340.1 (Vickers' hardness) method, measure the steel of the embodiment of the invention and the hardness of SUS304 steel, its result sees table 3.
Test Example 3:IE (Erichsen number)
According to the GB4156 experimental technique, experiment material is the 0.5mm product, measures the steel of the embodiment of the invention and the IE of SUS304 steel, and its result sees table 3.
Test Example 4:LDR (Limit Drawing ratio)
According to the GB/T15825.3 experimental technique, experiment material is the 0.5mm product, measures the steel of the embodiment of the invention and the LDR of SUS304 steel, and its result sees table 3.
Test Example 5: tissue
Utilize the ferritic appearance to detect average martensite content (area percent) after the LDR experiment, its result sees table 3.
Table 3 the present invention implements to be listed as typical forming property contrast
Table 3 has been listed the contrast that the present invention implements to be listed as typical forming property index and conventional SUS304; The intensity of material of the present invention, hardness are starkly lower than conventional SUS304; And LDR, the martensite content after the material cold deformation of reflection material pull and stretch performance index obviously are superior to SUS304, and the IE of reflection material bulging performance index is not as conventional SUS304.Table 2, table 3 shown that fully material punching performance of the present invention is good, can avoid stamping cracking, can avoid the excellent properties of punching press process annealing.
Test Example 6: inclusion is formed and pattern
Adopt the contrast of control effect and conventional SUS304 of inclusion of the embodiment of the invention steel of transmissioning electric mirror determining to see Fig. 1 and table 4, table 5, wherein Fig. 1 a is the inclusion pattern of 18Cr-8Ni-0.009Al steel; Fig. 1 b is the inclusion pattern of the embodiment of the invention 1 steel; Table 4 is that the inclusion of 18Cr-8Ni-0.009Al steel is formed; Table 5 is that the inclusion of the embodiment of the invention 1 steel is formed.
The inclusion of table 418Cr-8Ni-0.009Al steel is formed
| Element | Wt％ | At％ |
| OK | 33.65 | 48.24 |
| MgK | 14.13 | 13.33 |
| AlK | 36.82 | 31.29 |
| SiK | 00.59 | 00.49 |
| CaK | 02.40 | 01.37 |
| TiK | 00.80 | 00.38 |
| CrK | 03.58 | 01.58 |
| MnK | 04.24 | 01.77 |
| FeK | 03.79 | 01.56 |
| Matrix | Proofread and correct | ZAF |
Table 5 steel inclusion of the present invention is formed
| Element | Wt％ | At％ |
| OK | 15.11 | 33.62 |
| MgK | 02.60 | 03.81 |
| AlK | 04.15 | 05.47 |
| SiK | 08.42 | 10.67 |
| SK | 00.10 | 00.11 |
| CaK | 05.23 | 04.65 |
| TiK | 00.82 | 00.61 |
| CrK | 13.53 | 09.27 |
| MnK | 01.80 | 01.17 |
| FeK | 44.30 | 28.24 |
| NiK | 03.93 | 02.38 |
| Matrix | Proofread and correct | ZAF |
Wherein XK representes element X, Wt%: expression weight %, At%: expression atom %, ZAF: the modifying factor of quantitative analysis.
Visible from the contrast of Fig. 1 and table 4 and table 5, the Control and Inclusion Removal of material of the present invention more helps the drawing of material.
Test Example 7: the intensity under the cold roller and deformed rate condition of difference
Fig. 2 is seen in the contrast of the embodiment of the invention 1 steel and conventional SUS304 intensity under the cold roller and deformed rate condition of difference.
Visible from figure and since material of the present invention have lower Md30 (℃), material is starkly lower than SUS304 through the intensity after cold rolling, has the punching performance better than SUS304.
Claims (18)
1. austenitic stainless steel, the weight percent proportioning of its chemical ingredients is: C≤0.03%, Si≤0.75%, Mn:2.0-3.5%; Cr:16-19%, Ni:8.0-9.50%, Cu:2.0-3.0%; Nb:0.1-0.25%, N≤0.03%, Al≤0.005%; The content of Nb, C, N must satisfy simultaneously: Nb-8 (C+N)>=0, (C+Nb)≤0.30%, all the other are Fe and unavoidable impurities.
2. austenitic stainless steel as claimed in claim 1 is characterized in that, C≤0.02%.
3. austenitic stainless steel as claimed in claim 1 is characterized in that C:0.007-0.02%.
4. like the arbitrary described austenitic stainless steel of claim 1-3, it is characterized in that Si:0.20-0.70%.
5. like the arbitrary described austenitic stainless steel of claim 1-4, it is characterized in that Mn:2.5-3.45%.
6. like the arbitrary described austenitic stainless steel of claim 1-5, it is characterized in that Al:0.003-0.005%.
7. like the arbitrary described austenitic stainless steel of claim 1-6, it is characterized in that Cr:16.1-18.8%.
8. like the arbitrary described austenitic stainless steel of claim 1-7, it is characterized in that Ni:8.05-9.0%.
9. like the arbitrary described austenitic stainless steel of claim 1-8, it is characterized in that Cu:2.05-2.95%.
10. like the arbitrary described austenitic stainless steel of claim 1-9, it is characterized in that Nb:0.15-0.25%.
11., it is characterized in that N:0.005-0.02% like the arbitrary described austenitic stainless steel of claim 1-10.
12., it is characterized in that P≤0.03%, S≤0.02% like the arbitrary described austenitic stainless steel of claim 1-11.
13., it is characterized in that Md30 ℃≤-20 ℃ like the arbitrary described austenitic stainless steel of claim 1-12.
14., it is characterized in that said steel has than 6.0 grades of more tiny metallographic structures like the arbitrary described austenitic stainless steel of claim 1-13.
15. the method for manufacture like the arbitrary described austenitic stainless steel of claim 1-14 comprises:
In smelting process, basicity of slag is controlled at 1.5-2.5, under vacuum or non-vacuum condition, adopts aluminium content to be lower than ferrosilicon or the silicomanganese deoxidation of 1.0wt%, under the non-oxidation protective condition, pours into steel ingot or steel billet through abundant sedative molten steel;
Hot rolling and cold rolling;
Material heat treatment process after cold rolling be 1010-1070 ℃ fast cold, guarantee to obtain than 6.0 grades of more tiny metallographic structures.
16. method as claimed in claim 15 is characterized in that, said fast cold be water-cooled or air-cooled.
17., it is characterized in that the heating and temperature control that is fit in the hot rolling is at 1200-1240 ℃ like claim 15 or 16 described methods.
18., it is characterized in that cold rolling middle passage maximum distortion rate is 35% like the arbitrary described method of claim 15-17.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103411815A (en) * | 2013-07-31 | 2013-11-27 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for measuring martensite content in heat rolling dual-phase steel |
| CN104120370A (en) * | 2014-07-29 | 2014-10-29 | 包头市泽傲科贸有限公司 | Blade of sorting machine |
| JP2016538422A (en) * | 2013-10-28 | 2016-12-08 | ザ・ナノスティール・カンパニー・インコーポレーテッド | Metal steel production by slab casting |
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| JP2001081535A (en) * | 1999-09-16 | 2001-03-27 | Nisshin Steel Co Ltd | Austenitic stainless steel and steel sheet for press forming, excellent in formability and hot workability |
| CN1364944A (en) * | 2001-01-09 | 2002-08-21 | 日新制钢株式会社 | Austenite stainless steel wire low cracking sensitivity during forming and its preparing method |
| CN101845598A (en) * | 2009-03-23 | 2010-09-29 | 盐城中油船舶海洋工程科技有限公司 | Seawater corrosion resistant austenitic stainless steel and application thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001081535A (en) * | 1999-09-16 | 2001-03-27 | Nisshin Steel Co Ltd | Austenitic stainless steel and steel sheet for press forming, excellent in formability and hot workability |
| CN1364944A (en) * | 2001-01-09 | 2002-08-21 | 日新制钢株式会社 | Austenite stainless steel wire low cracking sensitivity during forming and its preparing method |
| CN101845598A (en) * | 2009-03-23 | 2010-09-29 | 盐城中油船舶海洋工程科技有限公司 | Seawater corrosion resistant austenitic stainless steel and application thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103411815A (en) * | 2013-07-31 | 2013-11-27 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for measuring martensite content in heat rolling dual-phase steel |
| JP2016538422A (en) * | 2013-10-28 | 2016-12-08 | ザ・ナノスティール・カンパニー・インコーポレーテッド | Metal steel production by slab casting |
| JP2019214076A (en) * | 2013-10-28 | 2019-12-19 | ザ・ナノスティール・カンパニー・インコーポレーテッド | Metal steel production by slab casting |
| CN104120370A (en) * | 2014-07-29 | 2014-10-29 | 包头市泽傲科贸有限公司 | Blade of sorting machine |
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Effective date of registration: 20190827 Address after: The Hong Kong Industrial Zone in Luoyuan Bay Development Zone of Luoyuan County of Fuzhou City, Fujian province 350600 Patentee after: Baosteel Desheng Stainless Steel Co., Ltd. Address before: 580 Baoshan District Changjiang Road, Shanghai, No. 200431 Patentee before: Baosteel Stainless Steel Co.,Ltd. |