CN117344238B - An environmentally friendly low Young's modulus super-free-machining ferritic stainless steel, its preparation method and its application - Google Patents
An environmentally friendly low Young's modulus super-free-machining ferritic stainless steel, its preparation method and its applicationInfo
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- CN117344238B CN117344238B CN202311273154.3A CN202311273154A CN117344238B CN 117344238 B CN117344238 B CN 117344238B CN 202311273154 A CN202311273154 A CN 202311273154A CN 117344238 B CN117344238 B CN 117344238B
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/52—Manufacture of steel in electric furnaces
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- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0075—Treating in a ladle furnace, e.g. up-/reheating of molten steel within the ladle
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- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
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- C22C33/04—Making ferrous alloys by melting
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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Abstract
本发明提供了一种环保型低杨氏模量超易切削铁素体不锈钢、其制备方法及其应用，成分以质量百分比计：C：0.008～0.012％，Si：≤0.2％，Mn：1.3～1.6％，P：0.004～0.008％，S：0.28～0.32％，Cr：13.4～13.9％，Al：6.5～6.9％，Mo：0.6～0.8％，Nb：0.02～0.04％，Sn：0.04～0.06％，Se：0.008～0.012％，Te：0.016～0.023％，Bi：0.07～0.09％，Mg：0.0002～0.0018％，N：≤0.008％，O：≤0.006％，以及余量的Fe和不可避免的杂质。本发明采用EAF‑AOD‑LF‑(锻造)‑(修磨)‑热轧‑拉拔剥皮‑退火1‑(冷拔1‑退火2)‑冷拔2工艺，最终制得线材，材料织构为强{110}、弱{012}丝织构，冷变形态杨氏模量为141GPa。本技术方案应用于圆珠笔笔头材料，有望替代镍白铜材料作为中油笔笔头材料；应用于中性笔笔头材料具有成本低，且书写阻尼感低的优势。
This invention provides an environmentally friendly low Young's modulus super-free-machining ferritic stainless steel, its preparation method, and its applications. The composition, by mass percentage, is as follows: C: 0.008–0.012%, Si: ≤0.2%, Mn: 1.3–1.6%, P: 0.004–0.008%, S: 0.28–0.32%, Cr: 13.4–13.9%, Al: 6.5–6.9%, Mo: 0.6–0.8%, Nb: 0.02–0.04%, Sn: 0.04–0.06%, Se: 0.008–0.012%, Te: 0.016–0.023%, Bi: 0.07–0.09%, Mg: 0.0002–0.0018%, N: ≤0.008%, O: ≤0.006%, and the balance being Fe and unavoidable impurities. This invention employs the EAF-AOD-LF-(forging)-(grinding)-hot rolling-drawing and peeling-annealing 1-(cold drawing 1-annealing 2)-cold drawing 2 process to finally produce wire with a material texture of strong {110} and weak {012} filaments, and a Young's modulus of 141 GPa in the cold-deformed form. This technical solution, when applied to ballpoint pen tip materials, is expected to replace nickel-copper alloys as the tip material for gel pens; when applied to gel pen tip materials, it offers advantages such as low cost and low writing resistance.
Description
Technical Field
The invention relates to a metal material, in particular to environment-friendly low Young modulus super-free cutting ferrite stainless steel, a preparation method and application thereof.
Background
In the pen manufacturing industry, the ball pen head is used as a key component, and has very strict requirements on cutting performance, wear resistance and corrosion resistance of the used materials. Currently, common materials for ballpoint pens include lead brass, nickel-white copper, and super-machinable ferritic stainless steel. Lead brass and nickel-white copper are copper-based materials, and compared with free-cutting ferrite stainless steel, the lead brass and nickel-white copper have the characteristic of more excellent cutting performance, but the wear resistance and corrosion resistance are weaker than those of free-cutting ferrite stainless steel. The corrosion resistance and the wear resistance of nickel-white copper are higher than those of lead brass, but the price of the nickel-white copper is higher than that of lead brass, and the current lead brass material is basically replaced by nickel-white copper.
Although the super-easy-cutting ferrite stainless steel has the advantages of low cost, good corrosion resistance, good wear resistance and the like compared with nickel-white copper, the root cause of the super-easy-cutting ferrite stainless steel which is not substituted for the nickel-white copper is that the Young modulus of the super-easy-cutting ferrite stainless steel is higher than that of the nickel-white copper, and the super-easy-cutting ferrite stainless steel has harder hand feeling and strong damping feeling during writing. The nib material is typically matched to the ink material. At present, neutral ink used for a neutral pen with high requirements on writing smoothness and corrosion resistance is made of super-easy-cutting ferrite stainless pen head material, and organic solvent ink used for a medium-sized pen with high requirements on writing smoothness is made of nickel-white copper material. Because the middle oil pen is smoother to write compared with the neutral pen, the market prospect is wider.
In the field of super-machinable ferritic stainless steel, typical materials include SF20T from Shichen Special Seiko Co., ltd and DSR6F from Dachen Special Steel Co., ltd, which are free-cutting ferritic stainless steel components to which elements such as Pb and Te are added. Because Pb is a toxic element, the material has the risks of environmental pollution and harm to human health in the production, service and recovery processes, bi is used for replacing Pb to be the development trend of the current super-free cutting stainless steel field, and related enterprises and universities in China also apply for related patents, including the publication number of CN 109898025A, CN 10892999B, CN 11354392A, CN 111334712B, CN 108315643B, CN 109865804B.
The Young's modulus of the traditional Fe-Cr ferrite stainless steel in the cold transformation form is about 200GPa, the Young's modulus of the nickel-white copper (CuNi 12Mn5Pb 2) in the cold transformation form is about 115GPa, and the Young's modulus of the traditional Fe-Cr ferrite stainless steel is different by 73.9%, if the Young's modulus of the ultra-free cutting ferrite stainless steel can be greatly reduced, the ultra-free cutting ferrite stainless steel can be used for replacing the nickel-white copper to a certain extent in the ball pen head material field, and the writing damping feeling of a neutral pen can be reduced to a certain extent.
Disclosure of Invention
In order to solve the problems in the background art, the invention provides the environment-friendly low Young modulus super-cutting ferrite stainless steel, the preparation method and the application thereof, the cutting performance and the corrosion resistance of the environment-friendly low Young modulus super-cutting ferrite stainless steel are equivalent to those of the existing super-cutting ferrite stainless steel, the cost and the elastic modulus of the environment-friendly low Young modulus super-cutting ferrite stainless steel are greatly reduced, the environment-friendly low Young modulus super-cutting ferrite stainless steel can be applied to ball point pen point materials, is hopeful to replace nickel-copper materials to be used as medium oil pen point materials, and has the advantages of low cost and low writing damping feeling when being applied to neutral pen point materials. The material does not contain Pb, has good environmental protection, does not contain copper, has low cost and is easy to manufacture and use.
In order to achieve the above purpose, the invention adopts the following technical scheme:
The environment-friendly low Young modulus super-cutting ferrite stainless steel comprises ：C：0.008～0.012％,Si：≤0.2％,Mn：1.3～1.6％,P：0.004～0.008％,S：0.28～0.32％,Cr：13.4～13.9％,Al：6.5～6.9％,Mo：0.6～0.8％,Nb：0.02～0.04％,Sn：0.04～0.06％,Se：0.008～0.012％,Te：0.016～0.023％,Bi：0.07～0.09％,Mg：0.0002～0.0018％,N：≤0.008％,O：≤0.006％, parts by mass and the balance of Fe and unavoidable impurities, wherein the ferrite stainless steel material has strong {110} and weak {012} silk textures.
Preferably, the environment-friendly low Young modulus super-cutting ferrite stainless steel comprises ：C：0.009～0.012％,Si：≤0.04％,Mn：1.5～1.6％,P：0.004～0.008％,S：0.29～0.32％,Cr：13.5～13.9％,Al：6.7～6.9％,Mo：0.6～0.8％,Nb：0.03～0.04％,Sn：0.052～0.06％,Se：0.009～0.012％,Te：0.018～0.023％,Bi：0.082～0.09％,Mg：0.0006～0.0018％,N：≤0.003％,O：≤0.0012％, parts by mass of Fe and unavoidable impurities in balance.
Preferably, the environment-friendly low Young modulus super-cutting ferrite stainless steel is characterized in that the components meet the Te/Se mass ratio of 1.9-2.1.
Preferably, the raw materials are subjected to EAF-AOD-LF-die casting-forging-grinding-hot rolling in sequence to prepare the environment-friendly low Young modulus super-free cutting ferrite stainless steel wire, wherein the Young modulus in an annealed state is not higher than 156GPa and the Young modulus in a cold deformation state is not higher than 142GPa in the rolling process.
The components of the invention are specifically as follows:
carbon is an austenite forming element, and the carbon content should be as low as possible in order to ensure no austenite phase is formed and avoid the reduction of thermoplasticity caused by the precipitation of a small amount of austenite, and in addition, the carbon content should be as low as possible in order to ensure that the precipitation temperature of M23C6 type carbide is lower than the hot rolling temperature, but the carbon content is too low to increase the smelting cost. The manganese content is controlled to be 0.008-0.010wt%.
Si, si can reduce the activity of carbon in steel to a certain extent, reduce the Young's modulus of the material and reduce the plasticity of the material, and the three functions are similar to those of aluminum, but the effect of silicon on reducing the Young's modulus of the material is less obvious than that of aluminum, and the effect of silicon on reducing the plasticity of the material is more obvious than that of aluminum. The super-free-cutting ferrite stainless steel is added with a large amount of aluminum elements, and can be replaced by aluminum elements instead of silicon elements in practice, but the impurity Si elements are unavoidable in molten steel, scrap steel and alloy raw materials, and the highest addition amount of silicon is 0.2wt.% when the aluminum content reaches 6.5wt.% from the viewpoint of material plasticity. The invention only needs to control the silicon content below 0.2wt.%.
Mn is the basic forming element of free cutting phase sulfide and is also the key element for inhibiting FeS precipitation of hot brittle phase, and the content of Mn should be as high as possible, but Mn is also the austenite forming element and should be as low as possible to avoid austenite phase formation. The manganese content is controlled to be 1.3-1.6wt%.
P is used as a traditional grain boundary segregation element, is favorable for reducing the grain boundary binding force, reducing the plasticity of the material and improving the cutting chip breaking performance, can promote the segregation of tin on the surface of sulfide and improve the pitting corrosion resistance of the material, but can also promote the segregation of tin and bismuth on the ferrite grain boundary, and greatly reduce the thermoplasticity of the material. The phosphorus content of the invention is controlled to be 0.004-0.008wt%.
S is one of main free cutting elements, mainly exists in the form of sulfide, the cutting performance of the material is improved along with the increase of the sulfur content in steel, sulfide can be used as precipitation points of Bi simple substance, the increase of the sulfur content is favorable for the uniform distribution of the Bi simple substance in the steel, but the increase of the sulfur content reduces the thermoplasticity of the material. The sulfur content of the invention is controlled to be 0.28-0.32wt%.
Cr is ferrite forming element and has passivation effect in stainless steel, for traditional clean ferrite stainless steel, chromium content can reach 16wt.% to meet corrosion resistance requirement, but for free cutting steel, free cutting phase can reduce pitting corrosion resistance of material, chromium content is usually about 20wt.% to meet long-term service requirement of material in ink, and because of adding corrosion resistant element aluminum, chromium content can be reduced, alloy cost can be saved, in addition, chromium belongs to Young modulus element of ferrite, from Young modulus reduction, chromium content is lower and better. The chromium content is controlled to be 13.4-13.9wt%.
Al is a strong deoxidizing element in the steelmaking process, aluminum acts in steel in a similar way to chromium and silicon, aluminum is a ferrite forming element to reduce the activity of carbon in steel, aluminum is dissolved in steel to increase the lattice constant of steel, so that the Young modulus of the material is reduced, the strength (solid solution strengthening) of the material is improved, the plasticity of the material is reduced, the stacking fault energy of ferrite is reduced, the dynamic recrystallization and the dynamic recovery behavior of the material are affected, the cold deformation texture strength is also a corrosion resistant element, and passivation is achieved. In addition, aluminum oxide inclusions, which are aluminum deoxidization products, are another form of existence of aluminum in steel, and large-size hard aluminum oxide inclusions are harmful to cutting performance and are required to be subjected to inclusion modification treatment. The higher the aluminum content, the better from the angle of reducing the Young modulus of the material, but the higher the aluminum content, the lower the plasticity of the material, the cold drawing process needs to correspondingly increase cold drawing pass, and the cost and failure loss of the cold rolling process are increased. According to the invention, the aluminum content is controlled to be 6.5-6.9wt%.
The effect of Mo in the traditional super-free cutting ferrite stainless steel mainly relates to two aspects, namely, the inhibition of austenite phase precipitation, the prevention of hot shortness caused by multiphase structures and the improvement of pitting corrosion resistance of the material. The invention can completely inhibit the possibility of austenite phase precipitation due to the addition of a large amount of aluminum elements in the ferrite stainless steel, and only molybdenum elements are needed to be added from the point corrosion resistance angle, and the molybdenum content is controlled to be 0.6-0.8 wt%.
Nb is an MC carbide forming element, the precipitation temperature of M23C6 can be reduced, coarse M23C6 carbide is prevented from being precipitated in the hot rolling process, the excessive high precipitation temperature of MC carbide can be caused due to the excessive high content of Nb, the size of the precipitate is excessively large, the grain homogenization control in the hot rolling process is not facilitated, and the control aim of the niobium content is that MC carbide precipitation mainly occurs in the hot rolling finish rolling process. The niobium content is controlled to be 0.02-0.04 wt.%.
Sn, tin is offset in grain boundaries, the grain boundary binding force of the material is reduced, the cutting performance of the material is improved, tin is also an element for improving the pitting potential of stainless steel, tin is offset between an easy-cutting phase and a steel matrix, the corrosion resistance of the material is improved, the thermoplasticity of the material is greatly reduced due to the fact that the tin content is too high, the grain boundary offset of the bismuth element is inhibited to a certain extent by the tin, and the high-temperature thermoplasticity is improved to a certain extent by adding a small amount of tin into the steel. The tin content is controlled to be 0.04-0.06 wt%.
Se and Te, selenium and tellurium are both sulfide morphological elements that improve thermal morphology. The traditional super-cutting ferrite stainless steel adopts active oxygen and tellurium elements in molten steel to regulate sulfide form, the active oxygen in the molten steel is below 10ppm due to high aluminum content, selenium element is properly added to improve sulfide form, but excessive selenium and tellurium can reduce the melting point of composite inclusion (Mn, cr, fe) (S, se, te) and increase the cracking tendency in the thermal deformation process, and the composite inclusion (Mn, cr, fe) (S, se, te) can be decomposed in the cooling process after rolling to separate out (Mn, cr, fe) Te from the composite inclusion. The selenium content is controlled to be 0.008-0.010wt%, the tellurium content is controlled to be 0.016-0.023 wt%, and the mass ratio of Te/Se is preferably 1.9-2.1.
Bi is similar to lead, and exists in a simple substance form in steel, the Bi has better effect of improving the free cutting performance of stainless steel compared with lead, the higher the Bi content is, the better the cutting performance is, but the thermoplastic property of the Bi to the material is obviously reduced, the thermoplastic property is reduced along with the increase of the Bi content, and the Bi content is controlled to be 0.07-0.09 wt%.
Mg is mainly in the form of magnesia-alumina spinel in the material, magnesium treatment is carried out before alloying of bismuth, tellurium and selenium, alumina inclusions in molten steel are refined and dissociated, the alumina inclusions are converted into nano-scale magnesia-alumina spinel inclusions, the magnesia-alumina spinel inclusions are not easy to polymerize and grow up, and the magnesia-alumina spinel inclusions can be used as nucleation particles of second phases such as aluminum nitride, sulfide and the like in the solidification process, so that the free-cutting phase is promoted to be uniformly distributed in steel. The magnesium content is controlled to be 0.0002-0.0018 wt%.
N is combined with aluminum element to form aluminum nitride inclusion, which has obvious effect of inhibiting the growth of solidified crystal grains, but the oversized aluminum nitride inclusion has adverse cutting performance. The present invention controls the nitrogen content to <0.008wt.%.
O because aluminum and magnesium are strong deoxidizing elements, oxygen exists mainly in the form of magnesia-alumina spinel in the steel. The oxygen content of the present invention is controlled at <0.006wt.%.
The invention relates to a preparation method of environment-friendly low Young modulus super-free cutting ferrite stainless steel, which comprises the following steps of:
(1) The EAF process comprises the steps of taking 400 series stainless steel waste as a raw material, adjusting the carbon content to be below 0.01wt.% in an oxidation period, coarsely adjusting the alloy components of molten steel according to the addition sequence of low-carbon ferrochrome-ferromolybdenum-aluminum iron in a reduction period, and controlling the smelting end temperature to be 1620-1630 ℃;
(2) The AOD process comprises the steps of sequentially adding molybdenum blocks, chromium blocks, low-carbon ferromanganese, ferroniobium, aluminum ingots, tin ingots and sulfur iron into molten steel, and adjusting the molybdenum, chromium, manganese, niobium, aluminum, tin and sulfur contents of the molten steel according to a target range, wherein the smelting end point temperature is 1540-1560 ℃;
(3) LF refining for at least 30min, feeding a magnesium-aluminum cored wire with the mass of 0.0004 times of molten steel into the molten steel under the condition of soft stirring of bottom blowing argon after refining, wherein the magnesium-aluminum cored wire comprises 5% of magnesium powder, 15% of aluminum powder and 85% of iron powder by mass percent, continuously soft stirring the molten steel for at least 5min after feeding, adding bismuth particles, tellurium particles, selenium particles and iron powder into an iron barrel in a mass ratio of 12:2:1:10, wherein the total addition amount of the bismuth particles, the tellurium particles, the selenium particles and the iron powder is 0.0032 times of the mass of the molten steel, inserting the iron barrel into the bottom of the steel ladle through a steel drill, and tapping after soft stirring the molten steel for at least 5min;
(4) The die casting process comprises the steps of performing metal solidification in a die casting mode, and controlling the pouring temperature of tapping at 1525-1535 ℃ to obtain a die cast ingot;
(5) The forging process comprises the steps of cogging a die cast ingot to a round billet with the diameter not more than 160mm, heating the die cast ingot to a temperature not less than 1150 ℃ before forging, soaking for at least 120min, forging, wherein the forging temperature is not less than 900 ℃ and the temperature of a billet is not less than the forging temperature, if the temperature of the billet is lower than the forging temperature in the forging process, the billet needs to be returned to the furnace for heating, and the heat preservation time is at least 30min, the single-pass deformation of the forging process is not more than 15%, air cooling the die cast ingot to a temperature not more than 600 ℃ after forging, and then pit slow cooling to obtain a blank;
(6) The polishing process comprises the steps of carrying out surface scraping polishing treatment on the blank before hot rolling, and ensuring that the surface is bright and has no crack and air hole defects;
(7) The hot rolling process comprises the steps of adopting a reducing atmosphere in a heating furnace, heating at a heating rate below 600 ℃ not higher than 10 ℃ per minute, heating to 900-1000 ℃ at a heating rate of 12-15 ℃ per minute, heating to 1160 ℃ at a heating rate of 4-8 ℃ per minute, and preserving heat for 40-75 min; the hot rolling is divided into three stages, namely discontinuous dynamic recrystallization rolling, continuous dynamic recrystallization zone rolling, continuous dynamic recrystallization and non-recrystallization mixed crystal rolling;
The first stage of hot rolling is discontinuous dynamic recrystallization rolling, namely rolling by adopting a roughing mill set and a middle rolling mill set, wherein the initial rolling temperature is not lower than 1100 ℃, the first-pass and second-pass elongation coefficients are controlled to be not higher than 1.1, the subsequent single-pass elongation coefficient is controlled to be within the range of 1.25-1.42, the single-pass elongation coefficient is increased along with the increase of the pass, the final rolling temperature is not lower than 1050 ℃, and the air cooling is carried out for at least 5s after the rolling, so that the water cooling is carried out;
The second stage of hot rolling is continuous dynamic recrystallization rolling, namely rolling by adopting a pre-finishing mill group, wherein the initial rolling temperature is 970-980 ℃, the single-pass elongation coefficient is controlled within a range of 1.24-1.32, the single-pass elongation coefficient is in a decreasing trend along with the increase of pass, the final rolling temperature is not lower than 940 ℃, and water cooling is not needed after rolling;
The third stage of hot rolling is continuous dynamic recrystallization and non-recrystallization mixed crystal rolling, namely rolling by adopting a finishing mill group and a reducing sizing mill group, wherein the rolling temperature is increased as much as possible, the rolling mill is closed by cooling water, the single-pass elongation coefficient is controlled to be not higher than 1.24, the finishing temperature is not lower than 920 ℃, the wire laying temperature is not lower than 880 ℃, then the air cooling is carried out to 620-650 ℃, and then the air cooling is carried out to room temperature, thus obtaining the ferrite stainless steel wire.
Preferably, in the step (4), the ingot molding adopts an octagonal ingot or a round ingot so as to reduce the possibility of corner cracking during forging and heating, and the section size is reduced as far as possible so as to reduce the hot working compression ratio or the expansion coefficient.
Preferably, in the step (7), the wire rod is hot-rolled, the rolling total elongation coefficient is controlled to be not lower than 20 in the first stage of hot rolling, and the rolling total elongation coefficient is controlled to be not lower than 4 in the third stage of hot rolling.
Preferably, in the step (7), the second-stage rolling total elongation coefficient may be inferred from the hot rolling total elongation coefficient, the first-stage rolling total elongation coefficient, and the third-stage rolling total elongation coefficient. Second stage rolling total elongation coefficient=hot rolling total elongation coefficient/first stage rolling total elongation coefficient/third stage rolling total elongation coefficient.
Preferably, in the step (7), the method for preparing the environment-friendly low Young modulus super-cutting ferrite stainless steel wire rod of the invention comprises the steps of setting the cooling water quantity of each rolling unit and whether a heat preservation cover is adopted to meet the rolling temperature and the cooling control requirement.
Preferably, in the step (7), the wire rod is hot rolled, and the rolling line speed is controlled within a range of [ (0.06-0.07) ×total elongation coefficient ] m/s. The value design is mainly influenced by the thermoplasticity of the material during the rolling in the third stage and is lower than the rolling line speed of the traditional free-cutting ferritic stainless steel 430F.
The invention relates to an application of environment-friendly low Young modulus super-free cutting ferrite stainless steel, which is characterized in that a wire rod of the ferrite stainless steel is sequentially subjected to a drawing peeling-annealing 1- (cold drawing 1-annealing 2) -cold drawing 2 treatment process to finally prepare a ferrite stainless steel silver bright wire rod for super-high-speed cutting processing of high-precision parts.
Preferably, the preparation method of the ferrite stainless steel silver bright wire comprises the following steps:
a. A drawing and peeling process, namely continuously drawing a ferrite stainless steel wire rod, controlling the drawing speed to be 9-10 m/min, controlling the peeling amount to be 0.1-0.3 mm, and controlling the drawing elongation coefficient to be 1.05-1.21 so as to enable the wire rod to reach the diameter of the wire rod in a required annealing state;
b. Annealing 1, namely carrying out on-line continuous annealing treatment on the wire rod subjected to the drawing and peeling treatment under the protection atmosphere condition, wherein the annealing temperature is not lower than 960 ℃, the heat preservation time is at least 5min,
C. Cold drawing 1-annealing 2, namely performing cold drawing treatment on the annealed wire, and performing cold drawing 1, wherein the single-pass or multi-pass drawing is performed, the single-pass drawing extension coefficient is controlled to be less than 1.26, the accumulated drawing extension coefficient before continuous annealing is controlled to be less than 1.52, the annealing 2 is performed, the annealing temperature is not lower than 920 ℃, the heat preservation time is 1-2 min, and the diameter of the annealed wire is determined by the final diameter of the wire and the drawing extension coefficient of the cold drawing 2 process;
d. And cold drawing 2, namely carrying out single-pass fine drawing on the annealed wire to obtain a final diameter, wherein the drawing elongation coefficient is controlled to be 1.15-1.22, so as to obtain the ferrite stainless steel silver bright wire, the material texture is strong {110}, weak {012} wire texture, and the Young modulus of the ferrite stainless steel silver bright wire in a cold transformation form is not higher than 142GPa.
Compared with the prior art, the invention has the following outstanding substantive features and remarkable advantages:
1. Compared with foreign SF20T or domestic prior art (CN 109898025A, CN 108929999B, CN 113584392A) alloy, the low Young modulus super-cutting ferrite stainless steel has the advantages that the cost is reduced by about 9000 yuan/ton, the process cost of smelting, hot rolling, annealing and the like is increased by about 1000 yuan/ton, the yield is equivalent to that of the prior art, the total production cost is reduced by about 8000 yuan/ton compared with that of the prior art, the annealed Young modulus of the low Young modulus super-cutting ferrite stainless steel is 156GPa, the Young modulus of the cold drawn state (finished wire) is 142GPa, and the reduction amplitude is 29.0 percent compared with that of the prior super-cutting ferrite stainless steel, the corrosion resistance and the wear resistance of the low Young modulus super-cutting ferrite stainless steel are equivalent to those of the prior super-cutting ferrite stainless steel, and the ferrite stainless steel applied to a neutral pen point material has the advantages of low cost and low writing damping sense;
2. the production cost of the low Young modulus super-free cutting ferrite stainless steel is only one third of that of nickel-copper, the Young modulus is 23.5% higher than that of nickel-copper (115 GPa), the corrosion resistance and the wear resistance are superior to those of nickel-copper, and the technical scheme can replace nickel-copper material to be used as a pen point material of a medium oil pen.
Drawings
Figure 1 shows a metallographic photograph (polishing) of a quarter of a longitudinal section of a wire in the example.
Figure 2 shows a metallographic photograph of a quarter of a longitudinal section of a wire (ferric chloride+hydrochloric acid solution attack) of an example.
FIG. 3 example one wire cross-section EBSD analyzes the face profile and the high angle grain boundary plot (> 15) of the axial (z) antipode plot.
The example of fig. 4 shows a wire cross-section EBSD analysis of axial (z) antipole.
FIG. 5 is a photograph of a ball point pen nib made of a wire material according to an embodiment.
Detailed Description
The following examples are given to illustrate and describe the technical solution of the present invention in detail, but are not to be construed as limiting the technical solution of the present invention.
Embodiment one:
In the embodiment, the environment-friendly low Young modulus super-cutting ferrite stainless steel comprises ：C：0.009％,Si：0.04％,Mn：1.5％,P：0.004％,S：0.29％,Cr：13.5％,Al：6.7％,Mo：0.6％,Nb：0.03％,Sn：0.052％,Se：0.009％,Te：0.018％,Bi：0.082％,Mg：0.0006％,N：0.003％,O：0.0012％, parts by mass of Fe and unavoidable impurities, wherein the ferrite stainless steel material has a strong {110} and weak {012} silk texture.
The preparation method of the environment-friendly low Young modulus super-free cutting ferrite stainless steel comprises the following steps of:
(1) Smelting by adopting a 20-ton electric arc furnace, after 400-series stainless steel scrap, pig iron and lime are added, starting to electrify and smelt, wherein the carbon content is 0.0052wt.% after the oxidation period is finished, and the alloy composition of molten steel is coarsely regulated according to the adding sequence of low-carbon ferrochrome-ferromolybdenum-ferroaluminum in the reduction period, wherein the smelting end temperature is 1620 ℃;
(2) The AOD process comprises the steps of sequentially adding molybdenum blocks, chromium blocks, low-carbon ferromanganese, ferroniobium, aluminum ingots, tin ingots and sulfur iron into molten steel, and adjusting the molybdenum, chromium, manganese, niobium, aluminum, tin and sulfur contents of the molten steel according to a target range, wherein the smelting end point temperature is 1550 ℃;
(3) The LF process comprises the steps of hanging a ladle to an LF station, measuring temperature, electrifying, adding Ca-Si powder in batches for reduction after slag is completely melted, refining for 30min, feeding 8kg of magnesium-aluminum cored wires into molten steel under the condition of soft stirring of bottom blowing argon after refining, wherein the magnesium-aluminum cored wires comprise 5% of magnesium powder, 15% of aluminum powder and 85% of iron powder by mass percent, continuing soft blowing argon for 5min after feeding, inserting a closed iron barrel containing 30.72kg of bismuth particles, 5.12kg of tellurium particles, 2.56kg of selenium particles and 25.6kg of iron powder into the bottom of the ladle through steel drills, and tapping after soft blowing argon and stirring for 5min;
(4) The die casting process comprises the steps of performing metal solidification in a die casting mode, controlling the pouring temperature of tapping at 1530 ℃, adopting a round ingot with the head diameter of 290mm and the tail diameter of 230mm for die casting, demoulding and cooling a billet, and cutting off a riser to obtain a die casting ingot;
(5) The forging process comprises the steps of cogging a die cast ingot to a round billet with the diameter of 150mm, forging the round billet at the heating temperature of 1150 ℃ for 120min, forging the round billet at the forging temperature of 1120 ℃, forging the round billet at the finish forging temperature of 920 ℃ and the single-pass deformation of less than 15%, forging the round billet with the diameter of 200mm, returning to the furnace for 30min, keeping the temperature of 1110 ℃, forging the round billet at the finish forging temperature of 960 ℃, and performing air cooling to 580 ℃ after forging, and pit entering and slow cooling to obtain a blank;
(6) The polishing process comprises the steps of carrying out surface scraping polishing treatment on the blank before hot rolling, and ensuring that the surface is bright and has no crack and air hole defects;
(7) The hot rolling process comprises heating furnace to 400 deg.C at 8 deg.C/min, heating to 600 deg.C at 9 deg.C/min, heating to 950 deg.C at 13 deg.C/min, heating to 1160 deg.C at 6 deg.C/min, and maintaining for 60min;
The first stage of hot rolling is discontinuous dynamic recrystallization rolling, namely rolling by adopting a roughing mill set and a middle rolling mill set, wherein the initial rolling temperature is 1120 ℃, the final rolling temperature is 1060 ℃, the size diameter after rolling is 31mm, and the guide rail is weakly water-cooled after 6s of transmission;
The second stage of hot rolling is continuous dynamic recrystallization rolling, namely rolling by adopting a pre-finishing mill group, wherein the initial rolling temperature is 975 ℃, and the final rolling temperature is 950 ℃, the size diameter after rolling is 15.5mm, and water cooling is not needed after rolling;
The third stage of hot rolling is continuous dynamic recrystallization and non-recrystallization mixed crystal rolling, namely rolling by adopting a finishing mill group and a reducing sizing mill group, wherein the rolling temperature is 940 ℃, the final rolling temperature is 925 ℃, the rolling line speed is controlled to be 40m/s, the wire laying temperature is 890 ℃, and then air cooling is carried out to room temperature after air cooling to 630 ℃, so that the dimension diameter of the finished ferrite stainless steel wire rod is 6mm. Specifically, the pass elongation coefficients are shown in table 1.
TABLE 1 Hot Rolling Process pass extension coefficient Table
The application of the environment-friendly low Young modulus super-free cutting ferrite stainless steel in the embodiment is that the ferrite stainless steel wire is sequentially subjected to the treatment process of drawing peeling-annealing 1- (cold drawing 1-annealing 2) -cold drawing 2, and finally the ferrite stainless steel silver bright wire is prepared and is used for super-high speed cutting processing of high-precision parts.
In this embodiment, the preparation method of the ferritic stainless steel silver bright wire includes the following steps:
a. A drawing and peeling process, namely continuously drawing a ferrite stainless steel wire rod, controlling the drawing speed to be 9m/min, controlling the peeling amount to be 0.2mm, and controlling the drawing extension coefficient to be 1.15, so that the wire rod reaches the diameter of the wire rod in the required annealing state, and the wire rod size after drawing and peeling is 5.4mm;
b. annealing 1, namely carrying out on-line continuous annealing treatment on the wire after the drawing and peeling treatment under the protection atmosphere condition, wherein the annealing temperature is 960 ℃, and the heat preservation time is 5min;
c. cold drawing 1-annealing 2 steps, namely drawing to 4.9mm in diameter, drawing to 4.4mm in diameter, continuously annealing at 920 ℃ for 2min at the annealing temperature, drawing to 4.0mm in diameter, drawing to 3.6mm in diameter, continuously annealing at 920 ℃ for 1.5min at the annealing temperature, drawing to 3.3mm, drawing to 3.0mm, continuously annealing at 920 ℃ for 1.5min at the annealing temperature, drawing to 2.8mm at the annealing temperature, drawing to 2.5mm at the annealing temperature, and continuously annealing at 920 ℃ for 1.0min at the annealing temperature;
d. And cold drawing 2, namely carrying out single-pass fine drawing on the annealed wire to the final diameter, and carrying out fine drawing to 2.3mm to obtain the ferrite stainless steel silver bright wire.
Test analysis:
The ferritic stainless steel silver bright wire prepared in example one was cut short, and as a sample, test analysis was performed to conduct microscopic observation of the longitudinal section and the cross section of the wire, and a metallographic photograph (polishing) of a quarter of the longitudinal section of the wire in example one of fig. 1. Figure 2 shows a metallographic photograph of a quarter of a longitudinal section of a wire (ferric chloride+hydrochloric acid solution attack) of an example. FIG. 3 example one wire cross-section EBSD analyzes the face profile and the high angle grain boundary plot (> 15) of the axial (z) antipode plot. The example of fig. 4 shows a wire cross-section EBSD analysis of axial (z) antipole. It can be seen from the figure that the structure is uniform, the inclusions are fine, and the free cutting phase is uniformly distributed in the steel. Example one material texture is a strong 110, weak 012 silk texture.
Embodiment two:
this embodiment is substantially the same as the first embodiment, and is characterized in that:
In the embodiment, the environment-friendly low Young modulus super-cutting ferrite stainless steel comprises ：C：0.012％,Si：0.04％,Mn：1.6％,P：0.008％,S：0.32％,Cr：13.9％,Al：6.9％,Mo：0.8％,Nb：0.04％,Sn：0.06％,Se：0.012％,Te：0.023％,Bi：0.09％,Mg：0.0018％,N：0.0028％,O：0.0011％, parts by mass of Fe and unavoidable impurities, wherein the ferrite stainless steel material has a strong {110} and weak {012} silk texture.
The preparation method of the environment-friendly low Young modulus super-free cutting ferrite stainless steel comprises the following steps of:
(1) Smelting by adopting a 20-ton electric arc furnace, after 400-series stainless steel scrap, pig iron and lime are added, starting to electrify and smelt, wherein the carbon content is 0.0052wt.% after the oxidation period is finished, and the alloy composition of molten steel is coarsely regulated according to the adding sequence of low-carbon ferrochrome-ferromolybdenum-ferroaluminum in the reduction period, wherein the smelting end temperature is 1630 ℃;
(2) The AOD process comprises the steps of sequentially adding molybdenum blocks, chromium blocks, low-carbon ferromanganese, ferroniobium, aluminum ingots, tin ingots and sulfur iron into molten steel, and adjusting the molybdenum, chromium, manganese, niobium, aluminum, tin and sulfur contents of the molten steel according to a target range, wherein the smelting end point temperature is 1560 ℃;
(3) The LF process comprises the steps of hanging a ladle to an LF station, measuring temperature, electrifying, adding Ca-Si powder in batches for reduction after slag is completely melted, refining for 30min, feeding 8kg of magnesium-aluminum cored wires into molten steel under the condition of soft stirring of bottom blowing argon after refining, wherein the magnesium-aluminum cored wires comprise 5% of magnesium powder, 15% of aluminum powder and 85% of iron powder by mass percent, continuing soft blowing argon for 5min after feeding, inserting a closed iron barrel containing 30.72kg of bismuth particles, 5.12kg of tellurium particles, 2.56kg of selenium particles and 25.6kg of iron powder into the bottom of the ladle through steel drills, and tapping after soft blowing argon and stirring for 5min;
(4) The die casting process comprises the steps of performing metal solidification in a die casting mode, controlling the pouring temperature of tapping at 1535 ℃, adopting a round ingot with the head diameter of 290mm and the tail diameter of 230mm for die casting, demoulding and cooling a billet, and cutting off a riser to obtain a die casting;
(5) The forging process comprises the steps of cogging a die cast ingot to a round billet with the diameter of 160mm, forging the die cast ingot at the heating temperature of 1150 ℃ for 120min, forging the die cast ingot at the forging temperature of 1120 ℃, forging the die cast ingot at the single-pass deformation of less than 15%, forging the die cast ingot at the final forging temperature of 920 ℃ to obtain a round billet with the diameter of 200mm, returning the die cast ingot to the furnace for 30min, forging the die cast ingot at the forging temperature of 1110 ℃, forging the die cast ingot at the single-pass deformation of less than 15%, forging the die cast ingot at the final forging temperature of 960 ℃ to obtain a round billet with the diameter of 160mm, cooling the die cast ingot to 600 ℃ after forging, and pit-entering slow cooling to obtain a blank;
(6) The polishing process comprises the steps of carrying out surface scraping polishing treatment on the blank before hot rolling, and ensuring that the surface is bright and has no crack and air hole defects;
(7) The hot rolling process comprises heating furnace to 400 deg.C at 8 deg.C/min, heating to 600 deg.C at 9 deg.C/min, heating to 950 deg.C at 13 deg.C/min, heating to 1160 deg.C at 6 deg.C/min, and maintaining for 75min in reducing atmosphere, wherein the hot rolling comprises three steps of discontinuous dynamic recrystallization rolling, continuous dynamic recrystallization zone rolling, continuous dynamic recrystallization and non-recrystallization mixed crystal rolling;
The first stage of hot rolling is discontinuous dynamic recrystallization rolling, namely rolling by adopting a roughing mill set and a middle rolling mill set, wherein the initial rolling temperature is 1120 ℃, the final rolling temperature is 1060 ℃, the size diameter after rolling is 31mm, and the guide rail is weakly water-cooled after 6s of transmission;
the second stage of hot rolling is continuous dynamic recrystallization rolling, namely rolling by adopting a pre-finishing mill group, wherein the initial rolling temperature is 980 ℃, and the final rolling temperature is 950 ℃, the size diameter after rolling is 15.5mm, and water cooling is not needed after rolling;
The third stage of hot rolling is continuous dynamic recrystallization and non-recrystallization mixed crystal rolling, namely rolling by adopting a finishing mill group and a reducing sizing mill group, wherein the rolling temperature is 940 ℃, the final rolling temperature is 925 ℃, the rolling line speed is controlled at 45m/s, the wire laying temperature is 890 ℃, and then air cooling is carried out to the room temperature after the air cooling is carried out to 650 ℃, so that the dimension diameter of the finished ferrite stainless steel wire rod is 6mm. The elongation coefficient of each pass in this example is the same as that in example one, and the elongation coefficient of each pass is shown in table 1.
The application of the environment-friendly low Young modulus super-free cutting ferrite stainless steel in the embodiment is that the ferrite stainless steel wire is sequentially subjected to the treatment process of drawing peeling-annealing 1- (cold drawing 1-annealing 2) -cold drawing 2, and finally the ferrite stainless steel silver bright wire is prepared and is used for super-high speed cutting processing of high-precision parts.
In this embodiment, the preparation method of the ferritic stainless steel silver bright wire includes the following steps:
a. A drawing and peeling process, namely continuously drawing a ferrite stainless steel wire rod, controlling the drawing speed to be 10m/min, controlling the peeling amount to be 0.3mm, and controlling the drawing extension coefficient to be 1.21, so that the wire rod reaches the diameter of the wire rod in the required annealing state, and the wire rod size after drawing and peeling is 5.4mm;
b. annealing 1, namely carrying out on-line continuous annealing treatment on the wire after the drawing and peeling treatment under the protection atmosphere condition, wherein the annealing temperature is 960 ℃, and the heat preservation time is 5min;
c. Cold drawing 1-annealing 2 steps, namely drawing to 4.9mm in diameter, drawing to 4.4mm in diameter, continuously annealing at 920 ℃ for 2min at the annealing temperature, drawing to 4.0mm in diameter, drawing to 3.6mm in diameter, continuously annealing at 920 ℃ for 1.5min at the annealing temperature, drawing to 3.3mm, drawing to 3.0mm, continuously annealing at 920 ℃ for 1.5min at the annealing temperature, drawing to 2.8mm at the annealing temperature, drawing to 2.5mm at the annealing temperature, and continuously annealing at 920 ℃ for 2.0min at the annealing temperature;
d. And cold drawing 2, namely carrying out single-pass fine drawing on the annealed wire to the final diameter, and carrying out fine drawing to 2.3mm to obtain the ferrite stainless steel silver bright wire.
Embodiment III:
This embodiment is substantially the same as the above embodiment, and is characterized in that:
In the embodiment, the environment-friendly low Young modulus super-cutting ferrite stainless steel comprises ：C：0.009％,Si：0.2％,Mn：1.3％,P：0.004％,S：0.28％,Cr：13.4％,Al：6.5％,Mo：0.6％,Nb：0.02％,Sn：0.04％,Se：0.008％,Te：0.016％,Bi：0.07％,Mg：0.0002％,N：0.003％,O：0.006％, parts by mass of Fe and unavoidable impurities, wherein the ferrite stainless steel material has a strong {110} and weak {012} silk texture.
The preparation method of the environment-friendly low Young modulus super-free cutting ferrite stainless steel comprises the following steps of:
(1) Smelting by adopting a 20-ton electric arc furnace, after 400-series stainless steel scrap, pig iron and lime are added, starting to electrify and smelt, wherein the carbon content is 0.0052wt.% after the oxidation period is finished, and the alloy composition of molten steel is coarsely regulated according to the adding sequence of low-carbon ferrochrome-ferromolybdenum-ferroaluminum in the reduction period, wherein the smelting end temperature is 1620 ℃;
(2) The AOD process comprises the steps of sequentially adding molybdenum blocks, chromium blocks, low-carbon ferromanganese, ferroniobium, aluminum ingots, tin ingots and sulfur iron into molten steel, and adjusting the molybdenum, chromium, manganese, niobium, aluminum, tin and sulfur contents of the molten steel according to a target range, wherein the smelting end point temperature is 1550 ℃;
(3) The LF process comprises the steps of hanging a ladle to an LF station, measuring temperature, electrifying, adding Ca-Si powder in batches for reduction after slag is completely melted, refining for 30min, feeding 8kg of magnesium-aluminum cored wires into molten steel under the condition of soft stirring of bottom blowing argon after refining, wherein the magnesium-aluminum cored wires comprise 5% of magnesium powder, 15% of aluminum powder and 85% of iron powder by mass percent, continuing soft blowing argon for 5min after feeding, inserting a closed iron barrel containing 30.72kg of bismuth particles, 5.12kg of tellurium particles, 2.56kg of selenium particles and 25.6kg of iron powder into the bottom of the ladle through steel drills, and tapping after soft blowing argon and stirring for 5min;
(4) The die casting process comprises the steps of performing metal solidification in a die casting mode, controlling the pouring temperature of tapping at 1530 ℃, adopting a round ingot with the head diameter of 290mm and the tail diameter of 230mm for die casting, demoulding and cooling a billet, and cutting off a riser to obtain a die casting ingot;
(5) The forging process comprises the steps of cogging a die cast ingot to a round billet with the diameter of 150mm, forging the round billet at the heating temperature of 1150 ℃ for 120min, forging the round billet at the forging temperature of 1120 ℃, forging the round billet at the finish forging temperature of 920 ℃ and the single-pass deformation of less than 15%, forging the round billet with the diameter of 200mm, returning to the furnace for 30min, keeping the temperature of 1110 ℃, forging the round billet at the finish forging temperature of 960 ℃, and performing air cooling to 580 ℃ after forging, and pit entering and slow cooling to obtain a blank;
(6) The polishing process comprises the steps of carrying out surface scraping polishing treatment on the blank before hot rolling, and ensuring that the surface is bright and has no crack and air hole defects;
(7) The hot rolling process comprises heating furnace with reducing atmosphere at temperature of 8 deg.C/min to 400 deg.C, 9 deg.C/min to 600 deg.C, 13 deg.C/min to 950 deg.C, 6 deg.C/min to 1160 deg.C, and heat preserving for 60min, wherein the hot rolling comprises three steps of discontinuous dynamic recrystallization rolling, continuous dynamic recrystallization zone rolling, continuous dynamic recrystallization and non-recrystallization mixed crystal rolling;
The first stage of hot rolling is discontinuous dynamic recrystallization rolling, namely rolling by adopting a roughing mill set and a middle rolling mill set, wherein the initial rolling temperature is 1120 ℃, the final rolling temperature is 1060 ℃, the size diameter after rolling is 31mm, and the guide rail is weakly water-cooled after 6s of transmission;
The second stage of hot rolling is continuous dynamic recrystallization rolling, namely rolling by adopting a pre-finishing mill group, wherein the initial rolling temperature is 975 ℃, and the final rolling temperature is 950 ℃, the size diameter after rolling is 15.5mm, and water cooling is not needed after rolling;
The third stage of hot rolling is continuous dynamic recrystallization and non-recrystallization mixed crystal rolling, namely rolling by adopting a finishing mill group and a reducing sizing mill group, wherein the rolling temperature is 940 ℃, the final rolling temperature is 925 ℃, the rolling line speed is controlled to be 40m/s, the wire laying temperature is 890 ℃, and then air cooling is carried out to room temperature after air cooling to 630 ℃, so that the dimension diameter of the finished ferrite stainless steel wire rod is 6mm. The elongation coefficient of each pass in this example is the same as that in example one, and the elongation coefficient of each pass is shown in table 1.
The application of the environment-friendly low Young modulus super-free cutting ferrite stainless steel in the embodiment is that the ferrite stainless steel wire is sequentially subjected to the treatment process of drawing peeling-annealing 1- (cold drawing 1-annealing 2) -cold drawing 2, and finally the ferrite stainless steel silver bright wire is prepared and is used for super-high speed cutting processing of high-precision parts.
In this embodiment, the preparation method of the ferritic stainless steel silver bright wire includes the following steps:
a. A drawing and peeling process, namely continuously drawing a ferrite stainless steel wire rod, controlling the drawing speed to be 9m/min, controlling the peeling amount to be 0.2mm, and controlling the drawing extension coefficient to be 1.15, so that the wire rod reaches the diameter of the wire rod in the required annealing state, and the wire rod size after drawing and peeling is 5.4mm;
b. annealing 1, namely carrying out on-line continuous annealing treatment on the wire after the drawing and peeling treatment under the protection atmosphere condition, wherein the annealing temperature is 960 ℃, and the heat preservation time is 5min;
c. cold drawing 1-annealing 2 steps, namely drawing to 4.9mm in diameter, drawing to 4.4mm in diameter, continuously annealing at 920 ℃ for 2min at the annealing temperature, drawing to 4.0mm in diameter, drawing to 3.6mm in diameter, continuously annealing at 920 ℃ for 1.5min at the annealing temperature, drawing to 3.3mm, drawing to 3.0mm, continuously annealing at 920 ℃ for 1.5min at the annealing temperature, drawing to 2.8mm at the annealing temperature, drawing to 2.5mm at the annealing temperature, and continuously annealing at 920 ℃ for 1.0min at the annealing temperature;
d. And cold drawing 2, namely carrying out single-pass fine drawing on the annealed wire to the final diameter, and carrying out fine drawing to 2.3mm to obtain the ferrite stainless steel silver bright wire.
Comparative example one:
comparative example one is a Pb-Te-S series super free cutting ferritic stainless steel material with the diameter of 2.3mm produced by a certain wire manufacturer in China.
Comparative example two:
the second comparative example is nickel-white copper material with the diameter of 2.3mm produced by a certain copper alloy manufacturer in China.
Table 2. Table of the proportions (wt.%) of the ingredients of the preferred and comparative examples of the invention
| Composition of the components | C | Si | Mn | P | S | Cr | Al | Mo | Nb | Sn |
| Example 1 | 0.009 | 0.04 | 1.5 | 0.004 | 0.29 | 13.5 | 6.7 | 0.6 | 0.03 | 0.052 |
| Example two | 0.012 | 0.04 | 1.6 | 0.008 | 0.32 | 13.9 | 6.9 | 0.8 | 0.04 | 0.060 |
| Example III | 0.009 | 0.02 | 1.3 | 0.004 | 0.28 | 13.4 | 6.5 | 0.6 | 0.02 | 0.040 |
| Comparative example one | 0.01 | 0.45 | 1.19 | 0.036 | 0.27 | 19.86 | - | 1.76 | - | - |
| Comparative example two | - | - | 5.8 | - | - | - | - | - | - | - |
| Composition of the components | Se | Te | Bi | Mg | N | O | Pb | Cu | Ni | Allowance of |
| Example 1 | 0.009 | 0.018 | 0.082 | 0.0006 | 0.0030 | 0.0012 | - | - | - | Fe |
| Example two | 0.012 | 0.023 | 0.090 | 0.0018 | 0.0028 | 0.0011 | - | - | - | Fe |
| Example III | 0.008 | 0.016 | 0.070 | 0.0002 | 0.0030 | 0.0012 | - | - | - | Fe |
| Comparative example one | - | 0.02 | - | - | - | - | 0.17 | - | - | Fe |
| Comparative example two | - | - | - | - | - | - | 1.5 | 43.1 | 12.3 | Zn |
TABLE 3 comparative effects of preferred and comparative examples of the present invention
As is evident from tables 1 to 3 above, the silicon content, chromium content and molybdenum content of the present invention are significantly lower than those of the comparative examples, and the metallic lead, copper and nickel are not contained, and the material cost is lower, compared with the comparative examples, in the above examples. The comparative examples are free of aluminum, niobium, tin, selenium, bismuth and magnesium. Aluminum is a strong deoxidizing element in a steelmaking process, aluminum acts in steel in a similar way to chromium and silicon, aluminum is a ferrite forming element to reduce the activity of carbon in steel, aluminum is dissolved in steel to increase the lattice constant of steel, so that the Young modulus of the material is reduced, the strength (solid solution strengthening) of the material is improved, the plasticity of the material is reduced, the stacking fault energy of ferrite is reduced, the dynamic recrystallization and dynamic recovery behaviors of the material are affected, the cold deformation texture strength is affected, and aluminum is also a corrosion resistant element to play a passivation role. In addition, aluminum oxide inclusions, which are aluminum deoxidization products, are another form of existence of aluminum in steel, and large-size hard aluminum oxide inclusions are harmful to cutting performance and are required to be subjected to inclusion modification treatment. The higher the aluminum content, the better from the angle of reducing the Young modulus of the material, but the higher the aluminum content, the lower the plasticity of the material, the cold drawing process needs to correspondingly increase cold drawing pass, and the cost and failure loss of the cold rolling process are increased. According to the invention, the aluminum content is controlled to be 6.5-6.9wt%. The Pb-Te-S series super-free cutting ferrite stainless steel material of the first comparative example is not added with aluminum element, has the Young modulus of 200GPa, cannot be used as a pen point material applied to a medium oil pen, and has higher writing damping sense. The second comparative example is a nickel-white copper material to which no aluminum element and no iron element were added. Bismuth is similar to lead, and exists in a simple substance form in steel, the bismuth has better effect of improving the free cutting performance of stainless steel compared with lead, the higher the bismuth content is, the better the cutting performance is, but the thermoplastic property of the bismuth to the material is obviously reduced, the thermoplastic property is reduced along with the increase of the bismuth content, and the bismuth content is controlled to be 0.07-0.09 wt%. The invention replaces lead with bismuth, and realizes the manufacture and use of environment-friendly free-cutting ferrite stainless steel. Tin can promote stainless steel pitting potential element, tin is offset between free cutting phase and steel matrix, so that corrosion resistance of material is raised, and tin has certain inhibiting effect on grain boundary offset of bismuth element. The tin content is controlled to be 0.04-0.06 wt%. Selenium is a sulfide morphological element for improving the thermal deformation morphology, and because the aluminum content of the material is high, the activity oxygen in molten steel is below 10ppm, and the selenium element is properly added to improve the sulfide morphology. The selenium content is controlled to be 0.008-0.010wt%. The comparative example contains no selenium, and sulfide morphology cannot be optimized by regulating and controlling the selenium content. Mg is mainly in the form of magnesia-alumina spinel in the material, magnesium treatment is carried out before alloying of bismuth, tellurium and selenium, alumina inclusions in molten steel are refined and dissociated, the alumina inclusions are converted into nano-scale magnesia-alumina spinel inclusions, the magnesia-alumina spinel inclusions are not easy to polymerize and grow up, and the magnesia-alumina spinel inclusions can be used as nucleation particles of second phases such as aluminum nitride, sulfide and the like in the solidification process, so that the free-cutting phase is promoted to be uniformly distributed in steel. The magnesium content is controlled to be 0.0002-0.0018 wt%. The comparative example does not contain an aluminum element, and therefore, no magnesium element is added. The material of the invention has strong {110} and weak {012} silk textures, and the Young's modulus in cold deformation state is 141GPa. The technical scheme is applied to a ball-point pen point material, is hopeful to replace nickel-copper material as a medium-oil pen point material, and has the advantages of low cost and low writing damping feeling when applied to a gel-ink pen point material, as shown in fig. 5. The tensile strength of the environment-friendly low Young modulus super-cutting ferrite stainless steel wire is obviously higher than that of the nickel-copper alloy material of the comparative example, but is equivalent to that of Pb-Te-S super-cutting ferrite stainless steel of the comparative example. The average service life of the ball-point pen head processing cutter manufactured by the wire material of the invention with the same specification and the average corrosion amount of 5%H 2SO4 soaked for 6 hours at normal temperature are equivalent to those of Pb-Te-S series super-free cutting ferritic stainless steel of comparative example one, and the corrosion resistance of the wire material of the invention is obviously superior to that of comparative example two. In a word, the cutting performance and corrosion resistance of the wire are equivalent to those of the existing super-cutting ferrite stainless steel material, the cost and the elastic modulus are greatly reduced, the material can be applied to a ball-point pen nib material, is hopeful to replace a nickel-copper alloy material to be used as a medium oil pen nib material, and has the advantages of low cost and low writing damping feeling when being applied to a neutral pen nib material. the material does not contain Pb, has good environmental protection, does not contain copper, has low cost and is easy to manufacture and use.
The embodiments of the present invention have been described above with reference to the accompanying drawings, but the present invention is not limited to the embodiments described above, and various changes, modifications, substitutions, combinations or simplifications made under the spirit and principles of the technical solution of the present invention can be made according to the purpose of the present invention, and all the changes, modifications, substitutions, combinations or simplifications should be equivalent to the substitution, so long as the purpose of the present invention is met, and all the changes are within the scope of the present invention without departing from the technical principles and the inventive concept of the present invention.
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| CN115786804A (en) * | 2022-11-28 | 2023-03-14 | 江阴华新特殊合金材料有限公司 | Low-Cr system soft magnetic stainless steel and control method of structure thereof |
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| CN115786804A (en) * | 2022-11-28 | 2023-03-14 | 江阴华新特殊合金材料有限公司 | Low-Cr system soft magnetic stainless steel and control method of structure thereof |
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