CN101228287A - High silicon stainless steel and material thereof and method for manufacturing high silicon stainless steel - Google Patents
High silicon stainless steel and material thereof and method for manufacturing high silicon stainless steel Download PDFInfo
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- CN101228287A CN101228287A CNA2005800511186A CN200580051118A CN101228287A CN 101228287 A CN101228287 A CN 101228287A CN A2005800511186 A CNA2005800511186 A CN A2005800511186A CN 200580051118 A CN200580051118 A CN 200580051118A CN 101228287 A CN101228287 A CN 101228287A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/04—Shaping in the rough solely by forging or pressing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
Abstract
Provided are a high silicon stainless steel exhibiting a great elongation at break, a spring manufactured by using such a stainless steel as a raw material, and a method for producing a high silicon stainless steel. The high silicon stainless steel is characterized in that it mainly consists of a fine structure having a crystal grain size of 15 [mu]m or less and exhibits an elongation at break of 12 % or more. It is preferable that the high silicon stainless steel mainly consists of a fine structure having a crystal grain size of 7 [mu]m or less and exhibits an elongation at break of 14 % or more. The high silicon stainless steel is further characterized in that it has an elongation at break after a thermal aging treatment of 7 % or more. The method for producing a high silicon stainless steel is characterized in that it comprises a loading step wherein an impact load and/or a static load is applied within the temperature range where no cracks occur in the high silicon stainless steel or the base alloy thereof when the surface temperature is not higher than 950 DEG C. By using such a high silicon stainless steel having a great elongation at break as a raw material, there can be produced a spring having a long life.
Description
Technical field
The present invention relates to a kind of high silicon stainless steel, particularly a kind of manufacture method with the high silicon stainless steel of high ductibility and the material of making and high silicon stainless steel.
Background technology
The title of high silicon stainless steel generally is silicon alloy (シ リ コ ロ ィ), is meant the metallic substance that contains the element silicon more than the 3.5 weight % in stainless steel.High silicon stainless steel is difficult for getting rusty, and is to have high tenacity, wearability and stable on heating metallic substance.
At that time, for high silicon stainless steel, the tension set after asuforging is handled was about 10%, and in addition, the tension set that carries out after thermal life is handled in the temperature about 500 ℃ in order to realize high rigidity mostly is 3.5% so lower value most.Therefore, because insufficient, exist in the problem that is restricted in the application of various mechanical parts etc. as the extensibility of one of prominent feature of metallic substance.
The steel of general stainless steel etc. can improve physical strength and ductility by reducing crystal grain.For the way of the reduction of steel such as stainless steel experience, have multiple record (for example patent documentation 1～3),
Patent documentation 1: the spy opens the 2000-248329 communique
Patent documentation 2: the spy opens the 2000-351040 communique
Patent documentation 3: the spy opens the 2002-192201 communique
Summary of the invention
But, when the method shown in the patent documentation 1～3 is applicable to high silicon stainless steel, still can generating material rimose phenomenon even attempt to the crystal grain granular of high silicon stainless steel, can not get the high silicon stainless steel of crystal grain granular.Particularly, the crystal grain grain-size of high silicon stainless steel hour is approximately 25～30 μ m at crystal grain, and tension set also do not reach as above-mentioned handle at asuforging that the back is about 10%, thermal life handle after the highest 3.5% level.
In order to solve such problem, by the high silicon stainless steel of realizing that breaking elongation is big, ductility is good, can bring into play the speciality of high silicon stainless steel more, good mechanical part etc. is provided.Therefore, strong high silicon stainless steel of wishing to have high tension set.
Therefore, in view of such background, the object of the present invention is to provide high silicon stainless steel with high tension set with and the material made and the manufacture method of high silicon stainless steel.
The present invention is that the method by the crystal grain granular of finding high silicon stainless steel realizes.That is, with when the surface temperature control of high silicon stainless steel or its mother alloy is in certain scope, by impact weight and/or dead weight, the impact weight of preferably loading forges, thereby can reduce the grain size of high silicon stainless steel.In addition, by changing surface temperature and the forging condition of being controlled, can control the size of crystal grain.
Being characterized as of high silicon stainless steel of the present invention, the size of crystal grain are based on the microscopic structure below the 15 μ m, and tension set is more than 12%.
Like this, for high silicon stainless steel, be controlled at below the 15 μ m by size, thereby can improve tension set crystal grain.
In addition, the preferred grain size of high silicon stainless steel of the present invention is based on the microscopic structure below the 7 μ m, and tension set is more than 14%.
Like this, for high silicon stainless steel, be controlled at below the 7 μ m, thereby can further improve tension set by size with crystal grain.
Here said high silicon stainless steel is meant more than the siliceous 3.5 weight %, is generally the stainless steel of 3.5 weight～7 weight %, for example シ リ コ ロ ィ A1, シ リ コ ロ ィ A2, シ リ コ ロ ィ D.
Wherein, " size of crystal grain " described here is meant the value of obtaining according to ASTM Designation E112-82, and " tension set " is the defined tension set of metal material stretching test method according to JIS standard Z2241.
In addition, the spring that uses high silicon stainless steel of the present invention to make as starting material owing to significantly improved ductility, though under the load of high loading also easy fracture not, good machinework can be provided.And, can also provide to have long-life spring.
In addition, high silicon stainless steel of the present invention is characterised in that with respect to above-mentioned various high silicon stainless steels after 480～550 ℃ temperature ranges were implemented the thermal life processing, unit elongation was more than 7% in breaking.Wherein, the thermal life processing mostly is in the said temperature scope for high silicon stainless steel and kept about 1 hour.
Handle by thermal life, can improve the hardness of material surface, but be that the high hardness of Brinell hardness number more than 450 can preserve value after high silicon stainless steel 7% or more was stated the thermal life processing on the implementation for tension set." Brinell hardness " described here is the letter of obtaining according to the static hardness test of JIS standard Z2243.
High silicon stainless steel with such high rigidity can provide good mechanical part, in addition, can also provide to tolerate more long-life spring of high loading.
Wherein, for mechanical parts such as springs, can carry out surface treatment by nitriding treatment or shot peening.Generally speaking rear surface hardness raising is invaded at nitrogen in the surface of high silicon stainless steel, can further improve surface hardness for the high silicon stainless steel with trickle crystal grain.In addition, shot peening can produce the effect of residual stress to high silicon stainless steel inside, if the high silicon stainless steel with trickle crystal grain that the surface hardness behind the intrusion nitrogen is improved carries out shot peening, because the caused residual stress of shot peening is easy to increase, thereby can resist bigger stress.
The manufacture method of high silicon stainless steel of the present invention is characterised in that, the mother alloy of high silicon stainless steel or high silicon stainless steel is carried out comprising in the forged operation operation of the loading of loading, promptly, in the surface temperature of high silicon stainless steel or mother alloy under the state more than 1100 ℃, apply after impact weight and/or the dead weight, surface temperature is not produce in the rimose temperature range below 950 ℃ and at high silicon stainless steel or mother alloy, apply impact weight and/or dead weight, can make the microscopic structure of grain size below 15 μ m like this is the steel of main body body.
So just can obtain to have the high silicon stainless steel of high breaking elongation.That is to say, when surface temperature is more than 1100 ℃, apply loading, can promote the granular of the crystal grain of high silicon stainless steel or its mother alloy like this up to the temperature below 950 ℃.At this moment, apply long forging, can reduce crystal grain in the temperature range below 950 ℃.In addition, do not produce the rimose temperature, in below 950 ℃,, can promote the granular of crystal grain by more applying loading under the low temperature at high silicon stainless steel or mother alloy.When in addition, the forged beginning time point surface temperature that is preferably high silicon stainless steel or its mother alloy is 1100～1200 ℃.The temperature that surpasses 1200 ℃ there is no need.If surface temperature is lower than 1100 ℃, if begin to forge, the high silicon stainless steel or its mother alloy that do not obtain abundant ductility as yet are easy to produce cracking.Wherein, " mother alloy " described here is meant the alloy that is made of certain composition, becomes high silicon stainless steel after forging.
In addition, the loading during forging can be a dead weight, if but apply impact weight, understand spontaneous activation and produce self-heating at high silicon stainless steel or its mother alloy inside, further promote the granular of crystal grain, can shorten the operation required time.In addition, can also and use dead weight and impact weight.For example, by after applying the load of impact weight, rolling (dead weight), can easily obtain the material of thin sheet form.
In addition, the manufacture method of high silicon stainless steel of the present invention is characterised in that, comprise: in the surface temperature of high silicon stainless steel or its mother alloy is after state more than 1100 ℃ applies impact weight and/or dead weight, surface temperature is reduced to below 950 ℃, and high silicon stainless steel or its mother alloy do not produce in the rimose temperature range, apply the first load loading operation of impact weight and/or dead weight; After under the surface temperature of high silicon stainless steel or its mother alloy is state in 850～1050 ℃ the scope time, beginning to apply impact weight and/or dead weight, surface temperature is reduced to below 950 ℃, and high silicon stainless steel or its mother alloy do not produce in the rimose temperature range, apply the second load loading operation of impact weight and/or dead weight; By the second load loading operation more than carrying out once after the first load loading operation, making grain size is that the following microscopic structure of 15 μ m is the steel of main body.
Do not produce under the rimose temperature at above-mentioned high silicon stainless steel or its mother alloy, and apply loading under the surface temperature below 950 ℃, can obtain the high silicon stainless steel of crystal grain granular, but by carrying out the first such load loading and the second load loading operation, high silicon stainless steel or mother alloy produce cracking in the time of can easily avoiding forging.In addition, in the second load loading operation, the surface temperature of high silicon stainless steel or its mother alloy can not surpass 1050 ℃ during the beginning applying load, and this is that crystal grain can be grown up once again because if be heated to above 1050 ℃.The second load loading operation can be carried out once, also can carry out repeatedly.
In addition, the manufacture method of high silicon stainless steel of the present invention is characterised in that, the minimum temperature of the surface temperature when applying loading in the second load loading operation, be lower than the minimum temperature of the surface temperature when applying loading in the first load loading operation, when carrying out repeatedly the second load loading operation, in the second load loading operation of repeatedly carrying out, when reducing one by one, the minimum temperature of the surface temperature when applying loading reduces the size of described crystal grain gradually, control the size of crystal grain by changing second number of times of loading the loading operation, making grain size is that the following microscopic structure of 15 μ m is the steel of main body.
Like this, can obtain having high tension set, the controlled high silicon stainless steel of grain size.
Lower limit temperature when applying loading by reducing gradually, crystal grain is diminished, that is, owing to increase the ductility of high silicon stainless steel or its mother alloy gradually, make that high silicon stainless steel or its mother alloy are difficult for producing cracking, applying loading each time can dwindle the size of crystal grain.
In addition, even the lowest temperature when not reducing applying load gradually applies repeatedly that crystal grain also diminishes in the loading, but in this case, for fear of the cracking of high silicon stainless steel or its mother alloy, the size that preferably will make great efforts to control the loading that applies is less than loading the most at the beginning.
The high silicon stainless steel that can provide tension set to improve, have good ductility is provided below the 15 μ m by the size with crystal grain.In addition, be reduced to below the 7 μ m, can provide tension set to leap the high silicon stainless steel that rises to more than 14% by size with crystal grain.
For handling the high silicon stainless steel that hardness improves through thermal life, the tension set of its material is more than 7%, can provide than prior art and compare the high silicon stainless steel that tension set significantly improves.At this moment, can to improve the fracture diffraction efficiency be more than 7% and Brinell hardness is a high silicon stainless steel more than 450.
Use the spring of high silicon stainless steel,,, but also have the long lifetime even it is also survivable to apply high loading owing to improved ductility by leaps and bounds as manufactured materials.
By the manufacture method of high silicon stainless steel of the present invention, can be so that the grain size of high silicon stainless steel be below the 15 μ m.
Description of drawings
Fig. 1 is the mode chart of forging method that is used for illustrating the high silicon stainless steel of embodiments of the invention, and the appearance when (a) expression is forged (b) is the stereographic map of the outward appearance of high silicon stainless steel.
Fig. 2 is the tissue of electron microscope observation of the high silicon stainless steel of embodiments of the invention 1, (a) shows (b) to be the photo of organizing of peripheral part by look-out station, and (c) be the photo of organizing of central part.
Fig. 3 is the explanatory view of butterfly spring of the high silicon stainless steel system of embodiments of the invention 1, (a) is the sectional drawing of looking from the front of the pad that constitutes butterfly spring, (b) sectional drawing of looking from the butterfly spring front.
Fig. 4 is the tissue of the electron microscope observation of high silicon stainless steel in the past, (a) shows (b) to be the photo of organizing of peripheral part by look-out station, and (c) be the photo of organizing of central part.
Nomenclature
1 mother alloy
2 steam hammers
3 anvil blocks
4 hammers
5 drive units
6 thermometers
7 operator
8 hold tool
101 high silicon stainless steels
30 pads
32 butterfly springs
Embodiment
Embodiments of the present invention below are described.
The high silicon stainless steel of present embodiment is based on the microcrystalline structure below the grain-size 15 μ m, and the fracture extensibility is more than 12%.And then based on the microcrystalline structure below the grain-size 7 μ m, the fracture extensibility is 14%.
Above-mentioned high silicon stainless steel can be used as the manufactured materials of the metal products of mechanical part etc. widely and uses.For example, use as manufactured materials, the rust-resisting property different with spring material in the past can be provided, have long-life spring by using above-mentioned high silicon stainless steel.
In addition, the high silicon stainless steel of present embodiment carries out the thermal life processing in 480～550 ℃ temperature range after, tension set is more than 7%.In addition, this high silicon stainless steel is handled through thermal life, can keep tension set more than 7%, and Brinell hardness is more than 450.By the high silicon stainless steel that use has such high rigidity, more anti-high loading can be provided and have long-life spring.
The granular of the tissue of high silicon stainless steel is to use the material of high silicon stainless steel or is undertaken by forming the mother alloy (being used as the general name of the material and the mother alloy of granular hereinafter referred to as " mother alloy ") that stainless composition constitutes.Be not particularly limited for the size of mother alloy etc., shape etc., can use roundwood, square bar, sheet material of all size etc. according to producing apparatus and purpose.In addition, in the manufacturing process that is undertaken by forging, be not limited to obtain being processed into the high silicon stainless steel of the roundwood, square bar, sheet material etc. of all size.
As described below, in certain temperature range, mother alloy is applied loading, make high silicon stainless steel simultaneously.Loading can be an impact weight, also can be dead weight, quickens for the speed that makes the crystal grain granular, preferably applies impact weight.Wherein, can exemplify the pressing machine of equipment hammer as the device that applies impact weight.
In order to obtain to have the high silicon stainless steel of trickle grain-size, below 950 ℃ mother alloy etc. is being forged, make the crystal grain granular of mother alloy etc.
For this manufacturing process, at first mother alloy that is heated to 1100～1200 ℃ for surface temperature etc. begins to make and applies loading.Owing to be subjected to the influence of surrounding environment, between applying load, the temperature of mother alloy etc. descends, even but the surface temperature of mother alloy etc. be reduced to below 950 ℃, also apply loading.Preferably in indehiscent temperature such as mother alloys, applying load under alap temperature.At this moment, when the temperature that is reduced to below 700 ℃, mother alloy etc. are easy to produce cracking, thereby will note more.
If obtain having the more tissue of the crystal grain of granular, and need be below 950 ℃, more preferably the temperature below 850 ℃ keeps temperature, simultaneously long-time applying load.And, in indehiscent temperature ranges such as mother alloy, forging up to alap temperature.
After applying load finished, the quenching method by in the past cooled off, and obtains the high silicon stainless steel of crystal grain granular.
Make the high silicon stainless steel of embodiments of the present invention by above method, as described below, by repeatedly carrying out the load (forging) of loading, can be easily the grain size of high silicon stainless steel be controlled between 0.6～15 μ m.
At first, near the mother alloy that is heated to 1100～1200 ℃ is begun to apply loading, rimose temperature range applying load (forging for the first time) does not take place up to the mother alloy below 950 ℃ etc.
Secondly, to heating such as mother alloys, make the surface temperature that stops forged mother alloy etc. reach more than 850 ℃, preferably near 1050 ℃.At this moment, if the surface temperature of mother alloy etc. surpasses 1050 ℃, crystal grain can increase on the contrary, so temperature can not be above 1050 ℃.And, reach near mother alloy 1050 ℃ etc. for surface temperature, begin applying load once again, up to below 950 ℃, preferred indehiscent temperature applying loads such as mother alloy (forging for the second time) below 850 ℃.Heat mother alloy once again, make the surface temperature of the mother alloy stop to apply loading etc. reach near 1050 ℃.And, reach near mother alloy 1050 ℃ etc. once again for surface temperature, begin to apply loading, up to the mother alloy below 950 ℃ the rimose temperature range not taking place applies loading (forging for the third time).And, as required, carry out the 4th time same forging repeatedly, forge for the 5th time and more the forging.
Here, the temperature when stopping to apply loading, low when forging for the first time for forging for the second time, can be easier to reduce the size of crystal grain.If reduce so forged lower limit temperature gradually, avoiding mother alloy generation rimose simultaneously, can apply high load, be easy to obtain trickle crystal grain.
As mentioned above, by carrying out above-mentioned forging process repeatedly,, reach the size of desirable crystal grain by the number of times of setting operation, thereby can control the size of crystal grain because the size of crystal grain reduces gradually.That is,, can obtain the microscopic structure of easier control grain size by forging process being divided into operation repeatedly.
Last in operation with above-mentioned same, cooled off by quenching in the past, obtains the high silicon stainless steel of present embodiment.
Below, specify by embodiment with reference to accompanying drawing, but the present invention is not limited to this embodiment.
Iron (Fe) main component (weight %) in addition is Si:4, C:0.02, Ni:7, and Cr:12 forges and quenches the mother alloy of diameter 12cm, the length 25cm of this sample ingredient, obtains the high silicon stainless steel of the long malicious 120cm of diameter 3cm.
The mode chart of the state when Fig. 1 is the forging of high silicon stainless steel of present embodiment.State when Fig. 1 (a) expression is forged, the face shaping of the high silicon stainless steel that Fig. 1 (b) expression obtains.
At first, the mother alloy 1 that is heated to 1150 ℃ is placed on 1/2 ton the anvil block 3 of steam hammer 2.
When the surface temperature of mother alloy 1 determines to reach 850 ℃ by thermometer 6, stop to forge, mother alloy 1 is put into the electric furnace that figure does not show, the surface temperature of mother alloy 1 is heated near 1050 ℃, be no more than 1050 ℃.The surface temperature of this mother alloy that is 1 is still measured by thermometer 6.Thermometer 6 uses digital radiation thermometer (Datong District's special steel (strain) is made, ス one サ one モ DS-06CF).
Then, use with above-mentioned same method and forge once again being heated near 1050 ℃ mother alloy 1, at this moment, forge the surface temperature that proceeds to mother alloy 1 when being 800 ℃ till.Afterwards, mother alloy 1 is put into the electric furnace internal heating, make the surface temperature of mother alloy 1 reach 1000 ℃.
Then, adopt above-mentioned same method to forge once again near the mother alloy 1 that is heated to 1000 ℃, at this moment, forge the surface temperature that proceeds to mother alloy 1 when reaching 750 ℃ till, so just finished conducting forging processing.
And then, for the mother alloy 1 of having finished conducting forging processing,, make the surface temperature of mother alloy reach after 1000 temperature at the electric furnace internal heating, be commonly referred to as the Water Quenching of " エ ス テ ィ one ", obtain high silicon stainless steel 101.
The tensile strength of the high silicon stainless steel 101 that so obtains is 1134N/mm
2, tension set is 14%, Brinell hardness is 341.
Then, high silicon stainless steel 101 is handled 500 ℃ of thermal lifes of implementing 1 hour, the tensile strength of the high silicon stainless steel after this thermal life is handled is 1634N/mm
2, tension set is 10%, Brinell hardness is 461.
Wherein, in any case above-mentioned, all be the 14A4 test film of the regulation of making according to the metal tensile test sheet of JIS standard Z2201, carry out tension test according to the metal tensile test method of JIS standard Z2241, measure tensile strength and tension set.In addition, measure Brinell hardness according to JIS standard 2243.
High silicon stainless steel 101 after the above-mentioned thermal life processing is carried out ring cutting, observe near the part of periphery (peripheral part) of section and the part (central part) at close center, measure the size of crystal grain according to ASTM Designation E112-82.
Fig. 2 (a) summary shows the look-out station of the section of above-mentioned ring cutting, Fig. 2 (b) and (c) be respectively the high silicon stainless steel after the thermal life of look-out station of peripheral part and central part electron microscope organize photo.Wherein, the magnification of Fig. 2 (b) and photo (c) is 400 times.By Fig. 2 (b) and (c) more as can be known, do not find different between the tissue of peripheral part and central part, and no matter the size of crystal grain is peripheral part (with reference to figure 2 (b)), or central part (with reference to figure 2 (c)), all is 6.9 μ m.
Wherein, because the size of crystal grain is not received the influence that above-mentioned thermal life is handled, the grain size before and after the above-mentioned thermal life is identical.
In addition,, implement nitriding treatment, implement shot peening according to turbine mode in the past according to method in the past for the high silicon stainless steel after the above-mentioned thermal life processing.The Vickers' hardness on the surface of resulting like this high silicon stainless steel is 1400, and wherein hardness is to be estimated by wishart's test, and Vickers' hardness is to measure according to JIS standard Z2244.
For the high silicon stainless steel of present embodiment 1 is compared in the past high silicon stainless steel, surface to high silicon stainless steel and the sample above-mentioned same shape of commercially available (in the past) is observed with above-mentioned same method, obtain organizing photo, and measure the size of crystal grain by same method.
Fig. 4 (a) summary shows the look-out station of above-mentioned high silicon stainless steel sample in the past, Fig. 4 (b) and (c) be respectively the high silicon stainless steel after the thermal life of look-out station of peripheral part and central part electron microscope organize photo.Wherein, the magnification of Fig. 4 (b) and photo (c) is 400 times.At Fig. 4 (b) with (c), have outside some difference though find the grain size between aforesaid peripheral part and the central part, from photo, do not see the difference of the significant tissue between peripheral part and the central part.And, for high silicon stainless steel in the past, the size of crystal grain, (with reference to figure 4 (b)) is 27.2 μ m at peripheral part, (with reference to figure 2 (c)) is 24.9 μ m at central part.
Use the high silicon stainless steel 101 that obtains diameter 3cm, long 120cm among the embodiment 1 to make butterfly spring.
The making of butterfly spring is to make earlier the pad that constitutes butterfly spring, is forming a plurality of pads are overlapping.
Fig. 3 (a) is the sectional drawing of looking from the pad front that makes, and Fig. 3 (b) is the sectional drawing of looking from the butterfly spring front that makes.
In the making of the pad shown in Fig. 3 (a), at first high silicon stainless steel 101 (with reference to Fig. 1) is cut into diameter 3cm (30mm), long 10cm (100mm), become a plurality of columned materials.Then, for each columned material, the bottom surface of knocking cylinder becomes after the about 40mm of diameter, cut into the about 40mm of diameter, the about 2.5mm of thickness, afterwards, in the hole of the about 20mm of central authorities' processing diameter, edge part carries out R processing, forms the discoideus material of tool foraminous.
Then, the material stress application discoideus for this tool foraminous carries out bending, makes the middle portion projection, forms roughly horn-like, then, handles 500 ℃ of thermal lifes of implementing 1 hour, obtains pad 31.Wherein, the size at the main position of pad 31 is shown in Fig. 3 (c).
Then, shown in Fig. 3 (b) that 130 pads 31 are overlapping, make butterfly spring 32.
For butterfly spring 32, descend direction (arrow a, b) to apply loading thereon, carry out longevity test.Use the severo pulse generator trier in the test, apply loading with the circulation (10Hz) of per second 10 times, the loading amplitude is 4.5kN～3.2kN, even found that and apply 8,000,000 loadings, does not find that also special damage takes place butterfly spring.
Industrial application
High silicon stainless steel of the present invention can also be widely used in metallic article except spring, particularly also Needing can be used for high strength and the machineworks such as high wilful bearing, bolt and nut, the structural portion such as back shaft Part, cutter, cutting element etc.
In addition, the manufacture method of high silicon stainless steel of the present invention also be applicable to beyond the high silicon stainless steel separate out hard The stainless metal of change type can be thought the granular that can realize its tissue. Other precipitation hardening types are not The rust steel for example has SUS630.
Claims (8)
1. high silicon stainless steel is characterized in that: based on grain-size is microscopic structure below the 15 μ m, and the fracture extensibility is more than 12%.
2. high silicon stainless steel is characterized in that: based on grain-size is microscopic structure below the 7 μ m, and the fracture extensibility is more than 14%.
3. high silicon stainless steel as claimed in claim 1 or 2, it is to implement the high silicon stainless steel that thermal life is handled in 480～550 ℃ temperature range, it is characterized in that, the fracture extensibility is more than 7%.
4. high silicon stainless steel as claimed in claim 3 is characterized in that, Brinell hardness is more than 450.
5. use the spring of each described high silicon stainless steel manufacturing in the claim 1～4.
6. the manufacture method of a high silicon stainless steel, it is characterized in that, carry out in the forged operation at mother alloy high silicon stainless steel or high silicon stainless steel, by comprising that load loading operation is made grain-size is that microscopic structure below the 15 μ m is the steel of main body, wherein, described load loading operation is, be under 1100 ℃ the state in the surface temperature of above-mentioned high silicon stainless steel or above-mentioned mother alloy, apply impact weight and/or dead weight, afterwards, in above-mentioned surface temperature is below 950 ℃ and above-mentioned high silicon stainless steel or above-mentioned mother alloy do not take place to apply impact weight and/or dead weight in the rimose temperature range.
7. the manufacture method of a high silicon stainless steel is characterized in that, carries out comprising in the forged operation at the mother alloy to high silicon stainless steel or high silicon stainless steel:
In the surface temperature of high silicon stainless steel or its mother alloy is after state more than 1100 ℃ applies impact weight and/or dead weight, be reduced to below 950 ℃ and high silicon stainless steel or its mother alloy do not produce in the rimose temperature range in surface temperature, apply the first load loading operation of impact weight and/or dead weight;
After under the surface temperature of high silicon stainless steel or its mother alloy is state in 850～1050 ℃ the scope time, beginning to apply impact weight and/or dead weight, be reduced to below 950 ℃ and high silicon stainless steel or its mother alloy do not produce in the rimose temperature range in surface temperature, apply the second load loading operation of impact weight and/or dead weight;
By the second load loading operation more than carrying out once after the first load loading operation, making grain size is that the following microscopic structure of 15 μ m is the steel of main body.
8. the manufacture method of high silicon stainless steel as claimed in claim 7, it is characterized in that, the minimum temperature of the surface temperature when applying loading in the described second load loading operation, be lower than the minimum temperature of the surface temperature when applying loading in the described first load loading operation, when carrying out repeatedly the described second load loading operation, in the described second load loading operation of repeatedly carrying out, the minimum temperature of the surface temperature when applying loading reduces one by one, gradually reduce simultaneously described grain-size, control grain-size by the number of times that changes the described second load loading operation, making grain-size is that the following microscopic structure of 15 μ m is the steel of main body.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/JP2005/009072 WO2006123408A1 (en) | 2005-05-18 | 2005-05-18 | High silicon stainless steel, spring manufactured by using same as raw material, and method for producing high silicon stainless steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101228287A true CN101228287A (en) | 2008-07-23 |
| CN101228287B CN101228287B (en) | 2010-06-16 |
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| Application Number | Title | Priority Date | Filing Date |
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| CN2005800511186A Expired - Fee Related CN101228287B (en) | 2005-05-18 | 2005-05-18 | High silicon stainless steel and material thereof and method for manufacturing high silicon stainless steel |
Country Status (6)
| Country | Link |
|---|---|
| US (1) | US20090016925A1 (en) |
| EP (1) | EP1882755A4 (en) |
| CN (1) | CN101228287B (en) |
| AU (1) | AU2005331823B2 (en) |
| CA (1) | CA2608600A1 (en) |
| WO (1) | WO2006123408A1 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112626426A (en) * | 2020-12-25 | 2021-04-09 | 江苏新核合金科技有限公司 | Preparation method of high-silicon stainless steel flange material |
Family Cites Families (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3055104A (en) * | 1955-11-07 | 1962-09-25 | Lyon Inc | Method of preparing steel blanks for drawing |
| US3689325A (en) * | 1969-12-01 | 1972-09-05 | Int Nickel Co | Stainless steel having improved corrosion and fatigue resistance |
| SE416408B (en) * | 1977-06-14 | 1980-12-22 | Fagersta Ab | ELECTRIC WIRE WITH A NICE CORRECT STRUCTURE AND WAY TO MAKE IT |
| US4448617A (en) * | 1980-08-05 | 1984-05-15 | Aichi Steel Works, Ltd. | Steel for a vehicle suspension spring having good sag-resistance |
| JPS61253324A (en) * | 1985-04-30 | 1986-11-11 | Kawasaki Steel Corp | Production of chromic stainless steel sheet |
| IT1200101B (en) * | 1985-08-01 | 1989-01-05 | Centro Speriment Metallurg | HEAT TREATMENT PROCEDURE FOR STAINLESS STEEL ROD |
| CN1022421C (en) * | 1989-04-26 | 1993-10-13 | 山东工业大学 | Process for casting nodular graphite cast iron with as-cast ferrite by metal mould |
| JPH0463247A (en) * | 1990-06-29 | 1992-02-28 | Nisshin Steel Co Ltd | High strength and high ductility stainless steel |
| JPH0693388A (en) * | 1992-06-23 | 1994-04-05 | Nkk Corp | High si stainless steel excellent in corrosion resistance and ductilility-toughness and its production |
| JP3429535B2 (en) * | 1993-09-30 | 2003-07-22 | 北村 悦二 | Method of hardening precipitation hardening type high silicon duplex stainless steel and method of manufacturing hardened product using the same |
| JP3093091B2 (en) * | 1994-03-02 | 2000-10-03 | 国産部品工業株式会社 | Manufacturing method of metal gasket |
| JPH1099930A (en) * | 1996-09-27 | 1998-04-21 | Daido Steel Co Ltd | High speed hot forging method for high speed steel |
| JP3877590B2 (en) * | 2001-12-25 | 2007-02-07 | 日新製鋼株式会社 | Highly elastic metastable austenitic stainless steel sheet and its manufacturing method |
| JP4200520B2 (en) * | 2003-11-18 | 2008-12-24 | 敏郎 小田 | Method for producing grain refined high silicon stainless steel |
-
2005
- 2005-05-18 CA CA002608600A patent/CA2608600A1/en not_active Abandoned
- 2005-05-18 EP EP05741487A patent/EP1882755A4/en not_active Withdrawn
- 2005-05-18 US US10/590,340 patent/US20090016925A1/en not_active Abandoned
- 2005-05-18 CN CN2005800511186A patent/CN101228287B/en not_active Expired - Fee Related
- 2005-05-18 AU AU2005331823A patent/AU2005331823B2/en not_active Ceased
- 2005-05-18 WO PCT/JP2005/009072 patent/WO2006123408A1/en active Application Filing
Also Published As
| Publication number | Publication date |
|---|---|
| CN101228287B (en) | 2010-06-16 |
| EP1882755A1 (en) | 2008-01-30 |
| AU2005331823A1 (en) | 2006-11-23 |
| WO2006123408A1 (en) | 2006-11-23 |
| CA2608600A1 (en) | 2006-11-23 |
| US20090016925A1 (en) | 2009-01-15 |
| EP1882755A4 (en) | 2011-05-11 |
| AU2005331823B2 (en) | 2011-07-21 |
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