EP1352980A1 - Siliciumreicher nichtrostender stahl - Google Patents

Siliciumreicher nichtrostender stahl Download PDF

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EP1352980A1
EP1352980A1 EP00981731A EP00981731A EP1352980A1 EP 1352980 A1 EP1352980 A1 EP 1352980A1 EP 00981731 A EP00981731 A EP 00981731A EP 00981731 A EP00981731 A EP 00981731A EP 1352980 A1 EP1352980 A1 EP 1352980A1
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steel
steels
equivalent
strength
resistance
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EP1352980A4 (de
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Yoshiyuki Shimizu
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a high-silicon stainless steel having excellent corrosion resistance and high strength as fundamental characteristics and, in addition, having various characteristics such as fatigue resistance, heat resistance, castability and workability.
  • Typical metallic materials excellent in corrosion resistance are stainless steels.
  • the field of application of stainless steels covers a wide range and, in recent years, stainless steels are used for not only corrosion resistance material but also various materials that should have characteristics such as mentioned below.
  • the uses requiring fatigue resistance are, for example, springs, gears, driving shafts, and the like.
  • a special use is core wires of inter-tooth brush.
  • High Cr steels such as stainless steels, are generally excellent in heat resistance.
  • the resistance against heat check (crack occurring due to thermal stress) is required in particular for rolls for continuous casting equipment, rolls for hot rolling, bearings for use at elevated temperatures, molds for die casting, molds for glass forming, and various heating furnace parts, among others.
  • Balls, rollers and other parts of bearing systems, supporting plates and rollers in quake-absorbing systems or supporting systems, dies, molds, tools, pressure vessel constituting materials and the like are required to have high crushing strength so that they can carry heavy loads.
  • Alloys for making precision casting products thin in thickness and complicated in shape are required to show good fluidity in a molten state on the occasion of casting and producing very few casting defects.
  • examples of such products are golf club heads, screws, impellers, turbine blades, pumps, valves and the like.
  • an alloy is used as a welding material, such as welding wire, welding rod, it is required to show good fluidity so that smooth and pretty beads can be formed.
  • Stainless steels are by nature corrosion-resistant materials. A higher level of corrosion resistance than the level required of ordinary stainless steels is required in the fields of semiconductor device production equipment parts, for example piping and connecting parts, medical instruments, food processing instruments and the like. In the production of semiconductors, high purity gases and pure water are used. Since these must not be contaminated with piping material-derived substances, the piping materials and connecting parts are required to have very good corrosion resistance.
  • Parts for bearing systems, supporting systems and the like, screws for chemical apparatus, various tools and the like are also required to have excellent wear resistance, though common to the property mentioned above (3).
  • metallic materials are required to have various properties and, in many cases, they are required to have several properties simultaneously.
  • the materials for tablet machines (tablet manufacturing machines) used in the pharmaceutical industry are required to have not only high corrosion resistance but also high strength and wear resistance so that the machines can resist deformation and wear during operation.
  • the materials are required to be as inexpensive as possible. This is because the material cost accounts for a great proportion of the total cost in the production of large-sized or mass-produced instruments and apparatus. However, very few materials can meet all of such requirements.
  • Iron(Fe)-based stainless steels are materials that are excellent in corrosion resistance and relatively inexpensive. Generally, high strength and good corrosion resistance are properties contradictory to each other in stainless steels. However, there are such stainless steel type alloys as mentioned below that are endowed with both.
  • JP Patent No. 619,383 JP Kokoku S46-9536
  • JP Patent No. 661,246 JP Kokoku S47-9899
  • JP Patent No. 1,167,791 JP Kokoku S57-17070
  • Silicolloy registered trademark
  • This steel is an alloy caused to have both high strength (high hardness) and good corrosion resistance by incorporating a relatively large amount of silicon (Si). It is also possible to give age hardenability to this steel by adjusting the chemical composition thereof.
  • the present inventor has been granted a patent (JP Patent No. 2,954,922) on a method of heat treatment of steel products for improving the aging behavior thereof.
  • the above-mentioned high-silicon stainless steel cannot yet fully satisfy such various requirements as mentioned above.
  • the above-mentioned piping materials for semiconductor production equipment are themselves required to have a high level of cleanness and, for producing meshes for use as filters, the material is required to have good drawability so that it can be worked into very thin wires.
  • corrosion-resistant metallic materials are used not only as forgings or rolled shapes but also as cast products (castings), hence good castability is also required.
  • the above-mentioned high-silicon stainless steel is a steel having a dual phase structure mainly composed of austenite and ferrite. Owing to its high Si content as compared with ordinary stainless steels, this steel has both corrosion resistance and high strength and shows good fluidity on the occasion of casting. Furthermore, as mentioned above, it can be provided with age hardenability through adjustment of the alloy composition, so that it is also possible to work that steel in a low-strength solid solution state and then causing the same to have high strength by the subsequent aging treatment. The products hardly deform upon aging treatment.
  • a concrete object of the present invention is to markedly improve the characteristics (1) to (7) mentioned above while taking advantage of the basic characteristics of the high-silicon stainless steel mentioned above.
  • the present inventor confirmed that the above object could be accomplished by increasing the index of cleanliness of the high-silicon stainless steel.
  • the index cleanliness of steel means the amount of inclusions, mainly oxides and sulfides.
  • a steel wherein these inclusions are reduced is referred to as a steel with a high index of cleanliness.
  • the present inventor confirmed that only when not only P, S and O but also C, Al, N (nitrogen) and H (hydrogen) are controlled, the above object can be accomplished.
  • the steel according to the present invention is a high-silicon stainless steel having the following chemical composition ("%” indicating "% by mass”):
  • a preferred embodiment of the above high-silicon stainless steel is as follows:
  • the steel contain at least one of the four components, namely 0.5 to 4% of Cu, 0.1 to 1.5% each of Nb, Ta and Ti, in addition to the above constituents. Further, residues of the Mg, Ca and rare earth elements used as refining agents may remain each at a level not exceeding 0.01%.
  • the contents of the main alloy components be adjusted in the following manner.
  • the Cr equivalent (X) is defined by the formula (1) given below
  • the Ni equivalent (Y) by the formula (2) given below, and adjustments are made so that these X and Y may satisfy the relations (3), (4) and (5) given below.
  • the above relation (3) represents the region above the straight line b in Fig. 1, the relation (4) the region below the straight line c in Fig. 1, and the relation (5) the region above the straight line d in Fig. 1. Therefore, it is the shaded region in Fig. 1 that satisfies the relations (3), (4) and (5) simultaneously.
  • the steel of the invention comprises 2 to 8% of Si, 8 to 25% of Cr and 4 to 16% of Ni as essential components.
  • Si is not only a main element providing the steel of the invention with strength but also provides the steel with heat resistance, oxidation resistance, corrosion resistance and high-temperature softening resistance as well. It is also an element lowering the melting point of the steel, and increases the fluidity and thereby improves the castability. When its content is below 2%, its effects of improving the above-mentioned characteristics are insufficient. On the other hand, since Si is a potent ferrite-forming element, the addition thereof in an excessive amount disturbs the basic structural balance of the steel of the invention. The upper limit has been set at 5% taking the influence on the Cr equivalent defined by the above formula (1) also into consideration. A more desirable Si content is 2.5 to 4-5%.
  • Cr is a component for securing the fundamental characteristics, namely corrosion resistance (in particular acid resistance), heat resistance and oxidation resistance, of the stainless steel. At below 8.0%, these properties are unsatisfactory. On the other hand, at Cr contents exceeding 25%, the Cr equivalent becomes large, the residual austenite increases and it becomes difficult to attain the desired mechanical properties.
  • Ni provides the steel with corrosion resistance, oxidation resistance and heat resistance and, in addition, is an element effective in maintaining the steel matrix in a desirable structural condition (dual phase structure composed of ferrite and austenite or three-phase structure composed of these and martensite) in balance with Cr.
  • a content of not less than 4% is necessary.
  • the austenite phase becomes excessive due to the increase in Ni equivalent, with the result that the mechanical properties deteriorate and the economical feature of the steel is lost.
  • a desirable Ni content is 5 to 15%.
  • the components which the steel of the invention may contain in addition to the above-mentioned Si, Cr and Ni, namely the optional additive components, are Mn, Cu, Co, Mo, Nb, Ta, Ti, W, V, B, Mg, Ca and rare earth elements (REMs). Only one of these may be added, or two or more of them may be added in combination.
  • the contents of the respective elements are optional provided that they do not exceed the respective upper limits given above. Of course, the content of the element not added becomes substantially 0 (zero) or at the impurity level. In the following, the effects and desirable contents of the above optional additive components are described.
  • Mn serves as a deoxidizing agent and at the same time is an austenite forming element.
  • Mn does not strongly influence the mechanical properties but serves to making the metallographic structure compact and stabilize the same.
  • a desirable content is 0,05 to 5%.
  • Cu is an element contributing to improvement in corrosion resistance (in particular acid resistance) and to precipitation hardening.
  • acid resistance in particular acid resistance
  • Cu impairs the hot workability of steel, hence the upper limit is 4%.
  • a content of 0.5 to 4% is desirable.
  • Mo increases the corrosion resistance of steel as well as the strength at elevated temperatures. It also contributes to improvements in toughness and wear resistance. For producing these effects satisfactorily, a content of not lower than 0.2% is desirable. On the other hand, since it is a ferrite forming element, an excessive content thereof leads to an increased Cr equivalent and this makes it difficult to obtain a desired structure. Further, Mo is an expensive element. Therefore, the content of Mo should be not more than 4%.
  • Nb, Ta and Ti contributes to increasing the strength of steel through its precipitation hardening effect.
  • Nb has an effect of increasing the hardened layer depth on the occasion of aging treatment. Therefore, when it is used as a material in thick-walled products, it serves to shorten the aging treatment time.
  • Ta has the same effects as Nb and, in addition, contributes to increasing the hardness in synergy with Cu, without impairing the corrosion resistance.
  • Ti contributes also to improvements in heat resistance and corrosion resistance, in addition to the above-mentioned precipitation hardening effect.
  • each of the four components namely the above three and Cu, may be selected for addition.
  • each of Nb, Ta and Ti causes decreases in hot workability and toughness at a content exceeding 3%, hence the upper limit should be set at 3% for each of them.
  • a desirable content is 0.1 to 1.5% for each.
  • Co is an element promoting austenite formation, as indicated by the formula (2) given above. Therefore, it has the effect supplementing the effect of Ni. Further, Co increases the age hardenability and thereby improves the strength (hardness) of products and, in addition, it also contributes to improvement in corrosion resistance. These effects become significant at 0.5% and above and the effects increase as the content increases. However, at an excessive level, the Ni equivalent becomes great and it becomes difficult to secure a desirable structure. Further, Co is an expensive component. Therefore, the upper limit has been set at 8%. When Co is added, its desirable content is 0.5 to 6%.
  • W increases the strength of steel at elevated temperatures and improves the creep resistance. At the same atom % level as Mo, it produces almost the same effects, so that it can be used in lieu of Mo or together with Mo. However, when it is added, an addition level up to 4% is sufficient. Considering that W is an expensive element, a desirable content is not higher than 1.5%.
  • V increases the precipitation hardenability and serves to improve the strength. It also increases the strength at elevated temperatures and improves the creep resistance. However, when V is excessive, the toughness of steel decreases, so that the content thereof should be suppressed to 4% or below. Desirable content is not higher than 1.5%.
  • B is effective in improving the hot workability and improving the toughness at elevated temperatures, among others. However, when B occurs in excess, the hot workability is rather impaired. Therefore, when it is added, it is necessary to suppress its content to 0.01% or below. A desirable content of B is not higher than 0.006%.
  • Mg, Ca and rare earth elements such as Y and Ce can be used as deoxidizing agents, desulfurizing agents and the like in the process of refining. These elements are effective in improving the hot workability of steel but, when they remain in the steel as oxide inclusions, the drawability of the steel is deteriorated. Therefore, even when these are added, their residue contents each should be not higher than 0.01%.
  • impurity elements are low and, when the contents of the seven elements to be mentioned below are all not higher than the respective specified levels, a steel excellent, on the whole, in the above-mentioned various characteristics can be obtained.
  • C is an element increasing the strength of steel and, generally, high strength steels contain a certain amount of C as an essential component.
  • the strength is secured by a specific metallographic structure brought about by Si, hence it is not essential that C be contained.
  • C is an element lowering the toughness of the steel of the invention and adversely affecting the workability, oxidation resistance and corrosion resistance thereof.
  • C is an element greatly influencing the Ni equivalent, as indicated by the formula (2) given above, so that when it occurs in excess, it becomes difficult to keep a balance with the contents of other components. Therefore, the content of C is recommendably as low as possible.
  • the content of C is suppressed to 0.04% or below. This is an allowable upper limit but, in the case of non-aging steel, in particular, the C content is desirably suppressed to 0.015% or below.
  • the current refining technology it is possible to produce even very low carbon steel with a C content of 0.01% or below.
  • P is a typical harmful impurity in stainless steel. It segregates in steel and deteriorates the mechanical properties, workability and corrosion resistance. Therefore, its content should be not more than 0.03% and should be suppressed to a level as low as possible. It is desirable that the content be not higher than 0.015%, preferably not higher than 0.010%.
  • S is a harmful element causing red shortness of steel and thereby lowers the hot workability of steel. It also impairs the cleanliness of steel via sulfide inclusions and deteriorates not only the mechanical properties (fatigue strength, cursing strength, etc.) but also the corrosion resistance and heat resistance (heat check resistance). Therefore, its content should be suppressed to 0.02% or below, desirably 0.01% or below. In particular in the case of a steel intended for the production of thin wires with a diameter of not greater than 0.1 mm, the content of S is desirably suppressed to 0.005% or below.
  • Al not more than 0.03% (desirably not more than 0.01%)
  • the allowable upper limit is set at 0.03%.
  • its content is desirably suppressed to 0.01% or below so that good drawability can be secured.
  • N not more than 0.05% (desirably not more than 0.03%)
  • N is an austenite forming element and, in some instances, it is actively added for stabilizing the austenite phase.
  • N is regarded as an impurity and the upper limit is imposed thereto.
  • the N content is desirably not more than 0.03% and as low as possible.
  • O oxygen
  • Oxgen forms oxide inclusions in steel and deteriorates the cleanliness index.
  • Such oxide inclusions lower the deformability of steel and, in particular in drawing, they cause wire breakage and make it impossible to produce thin wires.
  • the occurrence of such inclusions causes deterioration in surface cleanliness of steel products as well as decreases in corrosion resistance, fatigue strength, crushing strength and heat check resistance. Furthermore, they worsen the fluidity in the production of thin castings such as mentioned above. Therefore, the content of O is recommendably as low as possible. Although the allowable upper limit is 0.005%, it is desirable that the O content be further suppressed to 0.02% or less.
  • H is a very harmful component forming an interstitial solid solution in the matrix ferrite and austenite and causing hydrogen embrittlement. In addition, it causes decreases in toughness, fatigue strength and heat check resistance and, further, adversely affecting the castability. Therefore, the H content should be suppressed to a level as low as possible. While the allowable upper limit is 0.0003% (3 ppm), the H content is desirably not higher than 0.0002% (2 ppm).
  • Fig. 1 shows metallographic structures found upon solution heat treatment by water cooling from 1050°C.
  • the abscissa (X axis) denotes the Cr equivalent (Creq) and the ordinate (Y axis) denotes the Ni equivalent (Nieq).
  • the Cr equivalent and Ni equivalent are respectively calculated by the equations (1) and (2) given below.
  • Cr equivalent Cr (%) + 0.3 x Mo (%) + 1.5 x Si (%) + 0.5 x Nb (%)
  • Ni equivalent Ni (%) + 30 x C (%) + 0.5 x Mn (%) + 0.1 x Co (%)
  • the straight line a there is an austenite region or an "austenite + ferrite” region.
  • Below the straight line b there is a martensite region or a "martensite + ferrite” region.
  • the straight line c indicates the conditions for ferrite to amount to 5%
  • the straight line d indicates the conditions for ferrite to amount to 80%.
  • the structure of the matrix of the steel of the invention is desirably a dual phase structure comprising 5 to 80% of ferrite with the balance being austenite, or a three-phase structure comprising these two plus a slight proportion of martensite mixed in.
  • Such structure is included in the shaded region in Fig. 1. Therefore, it is understood that by selecting a chemical composition so that the following three relations can be satisfied simultaneously, the. above desirable structure can be obtained.
  • the structures shown in Fig 1 are structures found upon solution heat treatment. Even after aging treatment, the matrix structures do not show great changes from the states upon solution heat treatment, however. Upon aging treatment, various intermetallic compounds finely precipitate in the matrix and increase the strength (hardness). No problem arrives even when slight changes occur in the structure of the matrix itself.
  • austenite single phase steels or substantially austenite single phase steels with ferrite amounting less than 5% structures above the straight line c in Fig. 1
  • the required mechanical properties (strength, toughness, wear resistance, etc.) cannot be obtained.
  • dual phase structures composed of martensite and ferrite structures above the straight line c in Fig. 1)
  • the martensite single phase or martensite-ferrite dual phase structure provides high strength but poor corrosion resistance.
  • Below the straight line d the amount of ferrite is excessive and the strength and corrosion resistance are insufficient.
  • the region in which good mechanical properties and good corrosion resistance can be obtained is the region surrounded by the straight lines b, c and d, namely the region of dual phase structure composed of 5 to 80% ferrite and austenite or the region of three-phase structures composed of the two with martensite mixed in.
  • this straight line namely when the following relation (6) is satisfied, a three-phase structure composed of ferrite + austenite + martensite is formed.
  • Y 25.40 - 0.80X
  • composition adjustment be made so as to satisfy not only the relations (3) to (5) but also the relation (6), namely for the matrix structure to fall within the region below the straight line a in Fig. 1.
  • the steel of the present invention can be produced by the conventional method of melting stainless steels.
  • a steel melted in an electric furnace or converter for instance, is refined by remelting in a vacuum high frequency induction furnace or remelting in a vacuum arc furnace (VAR method) to remove impurity elements.
  • VAR method vacuum arc furnace
  • Other refining methods such as the vacuum electron beam melting method and the electroslag method (ESR method) in a nonoxidizing atmosphere, may also be used.
  • ESR method electroslag method in a nonoxidizing atmosphere
  • the high-silicon stainless steel according to the present invention includes one having age hardenability and one having no age hardenability. For both, solution heat treatment is essential.
  • the age hardenable steel may be used either as solution heat treated or after aging treatment following solution heat treatment for increasing the strength.
  • the steel as solution heat treated is low in strength (low in hardness) and is easy to work and, thus, it is also possible to perform forming in the state as solution heat treated and then conducting aging treatment to raise the strength to a desired level.
  • the aging treatment will not cause deformation of products and therefore is advantageous for the production of products required to have high dimensional precision.
  • the solution heat treatment is carried out by heating the alloy at a temperature from 950 to 1150°C and then cooling the same. At temperatures below 950°C, solid solution formation is insufficient and the amount of residual austenite increases, making it difficult to increase the strength. On the other hand, at temperatures exceeding 1150°C, crystal grains become coarse and the toughness decreases.
  • the time of heating is appropriately 1 to 2 hours per inch of product thickness.
  • the method of cooling is not particularly restricted but a rate of cooling at which a solid solution state can be obtained may be secured according to the product size (thickness). Thus, for example, water cooling, oil cooling or air cooling method can be employed.
  • the products after this solution heat treatment step have the dual phase structure comprising fine austenite and ferrite or the three-phase structure further comprising martensite, and the hardness is about HRC 34 to 38. Therefore, it is easy to subject the alloy in this solid solution state to machining to the desired shapes of the finished parts.
  • the aging treatment is carried out at 200 to 700°C. At low temperatures below 200°C or at high temperatures above 700°C, the desired hardness cannot be obtained.
  • a particularly desirable aging treatment temperature is within the range of 400 to 550°C. By treatment in such temperature range, high levels of hardness not lower than HRC 50 can be obtained.
  • the treatment temperature and treatment time can be selected according to the mechanical properties to be given to the products.
  • Fig. 2 and Fig. 3 Thirty-six steels specified in Fig. 2 and Fig. 3 were used as test materials. These steels could be divided into groups of three (e.g. steels Nos. 1 to 3, steels Nos. 4 to 6, ...) and the three in each group were of the same steel group.
  • one marked with ⁇ is a comparative steel having relatively high impurity levels
  • one marked with ⁇ is a steel according to the invention having a high cleanliness index with suppressed impurity levels
  • one marked with o ⁇ is a steel according to the invention having an ultrahigh cleanliness index with still further decreased impurity levels.
  • Steels Nos. 34, 35 and 36 are the conventional steels (commercial ones), corresponding to JIS SUS 304, SUS 630 and SUS 420 J2, respectively.
  • test material round bar was cut and machined into JIS No. 14 A test specimens for tensile test, which were subjected to tensile test at room temperature on a testing machine according to JIS B 7721. The tensile strength and elongation were determined.
  • Each test material round bar was cut to a diameter of 20 mm and a thickness of 10 mm and, after mirror polishing, the hardness was determined on a Rockwell hardness tester.
  • Each test material round bar was cut and machined into JIS No. 4A V-notched test specimens, and the Charpy impact strength was determined at room temperature using a testing machine according to JIS B 7722.
  • Test machine Ono-type rotating bending fatigue tester Frequency: 2000 rpm
  • Test temperature room temperature (in the atmosphere)
  • Test specimen diameter 12 mm, length 90 mm, parallel portion diameter 8 mm, parallel portion length 30 mm (R 20)
  • Balls 25.4 mm (1 inch) in diameter were cut out of each test material round bar and subjected to crushing strength measurement using an apparatus shown in Fig. 8.
  • the apparatus shown in Fig. 8 has a fixed tool 2 and a movable tool 3 each having a conical indentation and placed in a crushing cylinder 1.
  • the movable tool 3 is hydraurically moved up and down. Two specimens (steel balls) 4 were inserted into this crushing cylinder and the movable tool 3 was pressed down, and the load that caused crushing of the test specimens was recorded.
  • the fluidity of the molten steel was examined.
  • the groove 6 is 8 mm in width and has a rectangular section with a depth of 7 mm, and has a total length of 1 m.
  • a predetermined amount of each molten steel at 1600°C was poured into this groove through a central sprue 7, and the fluidity of each steel was evaluated in terms of the length of travel of the steel until coagulation. When this distance is longer, the fluidity is better, hence the castability is judged as good.
  • test material round bar was subjected to hot rolling and cold drawing and, after wire drawing to a diameter of 5.0 mm, further subjected to cold drawing using a diamond die while repeating heat treatment.
  • the drawability was evaluated in terms of the critical diameter allowing wire breakage whereby no more wire drawing was possible. When this value (critical wire diameter) is smaller, the drawability is better.
  • This test was applied to the test specimens (all after the above-mentioned solution heat treatment 1 alone) of steels Nos. 1 to 3 in Fig. 2 and steels Nos. 22 to 30 and 34 in Fig. 3.
  • Test specimens 8 having a shape (the shape of a bead on an abacus) as cut out from each test material round bar were surface-polished and subjected to 1000 heating-cooling cycles under the conditions given below and then examined for the occurrence of cracking. Heating: rapid heating in 6 seconds form room temperature to 750°C, followed by 2 seconds of maintenance at 750°C. Cooling: water cooling to 25°C in 3 seconds.
  • the heat check resistance was evaluated in terms of the number of cracks not shallower than 50 ⁇ m.
  • test material round bar was cut and machined into a diameter or 15 mm and a thickness of 10 mm, followed by mirror polishing to give test specimens.
  • the surface of each specimen was degreased and washed and immersed in 35% concentrated hydrochloric acid (25°C) for 8 hours. The specimens were then washed, dried, and weighed. The rate of corrosion (g/mm 2 ⁇ hr) was determined from difference between the weight before testing and that after testing.
  • Fig. 4 shows the results of testing of the precipitation hardening steels shown in Fig. 3 in the state of solid solution (without aging treatment), except for castability test results.
  • the high cleanliness steels (marked by ⁇ ) and ultrahigh cleanliness steels (marked by o ⁇ ) according to the invention are superior in all the test items, namely strength, elongation, toughness (Charpy impact values), fatigue strength, castability, heat check resistance and corrosion resistance, to the comparative steels.
  • the ultrahigh cleanliness steels with the levels of impurities suppressed to particularly low levels these improving effects are remarkable.
  • Fig. 5 shows the test results of sample materials obtained after further aging treatment following solution heat treatment of the precipitation hardening steels shown in Fig. 2.
  • the difference between the hardness after aging treatment and the hardness (hardness shown in Fig. 4) after solution heat treatment alone is shown for each steal under the heading "hardness difference". The greater this difference is, the greater the precipitation hardenability is.
  • Fig. 6 there are shown the test results of the non-precipitation type steels (steels Nos. 22 to 33) of the invention and the conventional steels (steels Nos. 34 to 36).
  • No. 35 is a precipitation hardening stainless steel, so that, in Test No. 62, the steel after aging treatment was used as the sample material while other sample materials were as obtained after solution heat treatment (No. 63 was subjected to quenching and tempering).
  • the high cleanliness steels and ultrahigh cleanliness steels of the invention were found to have greatly superior properties as compared with the comparative steels.
  • Fig. 7 shows the results of drawability test of the steels Nos. 1 to 3 shown in Fig. 2 and the steels Nos. 22 to 30 and 34 shown in Fig. 3. All the test samples used were as obtained after solution heat treatment. It can be seen that while the drawability limit was 40 ⁇ m for all the comparative steels, all the steels of the invention could be drawn to a diameter of 20 to 30 ⁇ m and, in particular, the ultrahigh cleanliness steels were comparable in drawability to SUS 304 (steel No. 34), which has the highest drawability among the conventional stainless steels.
  • the high-silicon stainless steel of the present invention has a number of excellent characteristics; as shown in the examples. Therefore, it can be used not only in the same fields of application as the conventional stainless steels but also in novel fields in which the conventional stainless steels cannot be applied. In particular, it is suited for use in those fields where a plurality of properties, such as corrosion resistance, heat resistance, wear resistance and fatigue resistance, are required simultaneously, as in the examples given at the beginning. It is also suited for use in producing very thin steel wires utilizing its excellent workability.
EP00981731A 2000-12-14 2000-12-14 Siliciumreicher nichtrostender stahl Withdrawn EP1352980A4 (de)

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PCT/JP2000/008877 WO2002048416A1 (fr) 2000-12-14 2000-12-14 Acier inoxydable a teneur elevee en silicium

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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AT502397B1 (de) * 2006-03-20 2007-03-15 Boehler Edelstahl Legierung für wälzlager
US7513960B2 (en) 2005-03-10 2009-04-07 Hitachi Metals, Ltd. Stainless steel having a high hardness and excellent mirror-finished surface property, and method of producing the same
EP2248918A1 (de) * 2008-02-29 2010-11-10 National Institute of Advanced Industrial Science And Technology Austenitischer edelstahl und wasserstoffentfernungsverfahren dafür
CN103842547A (zh) * 2011-07-29 2014-06-04 新日铁住金株式会社 高Si奥氏体系不锈钢的制造方法
EP1960992A4 (de) * 2005-12-07 2015-08-26 Sandvik Intellectual Property Musik-saite und instrument mit der saite
WO2018024763A1 (de) * 2016-08-05 2018-02-08 Flowserve Flow Control Gmbh EISENBASIERTE LEGIERUNG ZUR HERSTELLUNG THERMISCH AUFGEBRACHTER VERSCHLEIßSCHUTZSCHICHTEN
DE102016202885B4 (de) 2015-02-27 2022-01-05 Japan Silicolloy Industry Co., Ltd. Selektives Lasersinterverfahren
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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4002510A (en) * 1975-05-01 1977-01-11 United States Steel Corporation Stainless steel immune to stress-corrosion cracking
US4640817A (en) * 1983-08-05 1987-02-03 Sumitomo Metal Industries, Ltd. Dual-phase stainless steel with improved resistance to corrosion by nitric acid
EP0434887A1 (de) * 1989-12-20 1991-07-03 Nisshin Steel Co., Ltd. Hitzebeständiger austenitischer rostfreier Stahl
JPH0551633A (ja) * 1991-08-27 1993-03-02 Nippon Steel Corp 高Ｓｉ含有オーステナイト系ステンレス鋼の製造方法
JPH0874006A (ja) * 1994-09-08 1996-03-19 Nisshin Steel Co Ltd 強度及び捩り特性に優れたバネ用析出硬化型ステンレス鋼
JPH09256110A (ja) * 1996-03-18 1997-09-30 Kubota Corp ドリル加工性にすぐれた高靱性・高腐蝕疲労強度二相ステンレス鋼
JP2001107194A (ja) * 1999-09-29 2001-04-17 Nippon Shirikoroi Kogyo Kk 析出硬化型ステンレス鋼およびその製品の製造方法

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2750283A (en) * 1953-05-27 1956-06-12 Armco Steel Corp Stainless steels containing boron
JPS5456018A (en) * 1977-10-12 1979-05-04 Sumitomo Metal Ind Ltd Austenitic steel with superior oxidation resistance for high temperature use
JPS60177139A (ja) * 1984-02-23 1985-09-11 Daido Steel Co Ltd 超清浄鋼の製造方法
IE60553B1 (en) * 1989-12-21 1994-07-27 Paxlea Limited A computer system for portfolio management investment functions
JPH06287635A (ja) * 1993-03-31 1994-10-11 Nisshin Steel Co Ltd 延性に優れ溶接軟化のない高耐力・高強度ステンレス鋼材の製造方法
JPH08134596A (ja) * 1994-11-02 1996-05-28 Nippon Steel Corp 耐応力腐食割れ特性に優れた高強度ステンレス鋼板
JPH09302446A (ja) * 1996-05-10 1997-11-25 Daido Steel Co Ltd 二相ステンレス鋼
JP3596234B2 (ja) * 1996-05-29 2004-12-02 住友金属工業株式会社 オゾン含有水用ステンレス鋼材およびその製造方法
JPH09316602A (ja) * 1996-05-30 1997-12-09 Sumitomo Metal Mining Co Ltd 高強度、高耐食性２相ステンレス鋳鋼
JP3923163B2 (ja) * 1998-01-26 2007-05-30 日新製鋼株式会社 廃棄物焼却炉
JP3566069B2 (ja) * 1998-03-12 2004-09-15 住金ステンレス鋼管株式会社 ステンレス鋼管内面の被膜形成方法
JP2954922B1 (ja) * 1998-04-07 1999-09-27 日本シリコロイ工業株式会社 析出硬化型高珪素鋼製品の熱処理方法
JP2001059141A (ja) * 1999-08-18 2001-03-06 Sumitomo Metal Ind Ltd オーステナイト系ステンレス鋼および自動車排気系部品
JP4127447B2 (ja) * 1999-08-26 2008-07-30 日新製鋼株式会社 耐高温腐食性に優れた焼却炉体および焼却炉付帯設備

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4002510A (en) * 1975-05-01 1977-01-11 United States Steel Corporation Stainless steel immune to stress-corrosion cracking
US4640817A (en) * 1983-08-05 1987-02-03 Sumitomo Metal Industries, Ltd. Dual-phase stainless steel with improved resistance to corrosion by nitric acid
EP0434887A1 (de) * 1989-12-20 1991-07-03 Nisshin Steel Co., Ltd. Hitzebeständiger austenitischer rostfreier Stahl
JPH0551633A (ja) * 1991-08-27 1993-03-02 Nippon Steel Corp 高Ｓｉ含有オーステナイト系ステンレス鋼の製造方法
JPH0874006A (ja) * 1994-09-08 1996-03-19 Nisshin Steel Co Ltd 強度及び捩り特性に優れたバネ用析出硬化型ステンレス鋼
JPH09256110A (ja) * 1996-03-18 1997-09-30 Kubota Corp ドリル加工性にすぐれた高靱性・高腐蝕疲労強度二相ステンレス鋼
JP2001107194A (ja) * 1999-09-29 2001-04-17 Nippon Shirikoroi Kogyo Kk 析出硬化型ステンレス鋼およびその製品の製造方法

Non-Patent Citations (6)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 0173, no. 61 (C-1080), 8 July 1993 (1993-07-08) & JP 5 051633 A (NIPPON STEEL CORP), 2 March 1993 (1993-03-02) *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 07, 31 July 1996 (1996-07-31) & JP 8 074006 A (NISSHIN STEEL CO LTD), 19 March 1996 (1996-03-19) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 01, 30 January 1998 (1998-01-30) & JP 9 256110 A (KUBOTA CORP), 30 September 1997 (1997-09-30) *
PATENT ABSTRACTS OF JAPAN vol. 2000, no. 21, 3 August 2001 (2001-08-03) & JP 2001 107194 A (NIPPON SHIRIKOROI KOGYO KK), 17 April 2001 (2001-04-17) *
See also references of WO0248416A1 *
STAHL-EISEN: "Spurenelemente in Stählen" SPURENELEMENTE IN STAHLEN, DUSELDORF, VERLAG STAHLEISEN, DE, 1985, pages 19-34, XP002074494 *

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US7513960B2 (en) 2005-03-10 2009-04-07 Hitachi Metals, Ltd. Stainless steel having a high hardness and excellent mirror-finished surface property, and method of producing the same
US8097097B2 (en) 2005-03-10 2012-01-17 Hitachi Metals Ltd. Stainless steel having a high hardness and excellent mirror-finished surface property, and method of producing the same
EP1960992A4 (de) * 2005-12-07 2015-08-26 Sandvik Intellectual Property Musik-saite und instrument mit der saite
US7785531B2 (en) 2006-03-20 2010-08-31 Boehler Edelstahl Gmbh Alloy for roller bearing
AT502397B1 (de) * 2006-03-20 2007-03-15 Boehler Edelstahl Legierung für wälzlager
EP2248918A1 (de) * 2008-02-29 2010-11-10 National Institute of Advanced Industrial Science And Technology Austenitischer edelstahl und wasserstoffentfernungsverfahren dafür
EP2248918A4 (de) * 2008-02-29 2013-07-03 Nat Inst Of Advanced Ind Scien Austenitischer edelstahl und wasserstoffentfernungsverfahren dafür
CN103842547A (zh) * 2011-07-29 2014-06-04 新日铁住金株式会社 高Si奥氏体系不锈钢的制造方法
EP2738281A1 (de) * 2011-07-29 2014-06-04 Nippon Steel & Sumitomo Metal Corporation Verfahren zur herstellung eines austenitischen edelstahls mit hohem si-gehalt
EP2738281A4 (de) * 2011-07-29 2015-04-15 Nippon Steel & Sumitomo Metal Corp Verfahren zur herstellung eines austenitischen edelstahls mit hohem si-gehalt
US9243314B2 (en) 2011-07-29 2016-01-26 Nippon Steel & Sumitomo Metal Corporation Method for manufacturing high-Si austenitic stainless steel
DE102016202885B4 (de) 2015-02-27 2022-01-05 Japan Silicolloy Industry Co., Ltd. Selektives Lasersinterverfahren
WO2018024763A1 (de) * 2016-08-05 2018-02-08 Flowserve Flow Control Gmbh EISENBASIERTE LEGIERUNG ZUR HERSTELLUNG THERMISCH AUFGEBRACHTER VERSCHLEIßSCHUTZSCHICHTEN
US11590338B2 (en) 2016-12-19 2023-02-28 Abiomed, Inc. Heart pump with passive purge system

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