| 序号 | 专利名 | 申请号 | 申请日 | 公开（公告）号 | 公开（公告）日 | 发明人 |
|---|---|---|---|---|---|---|
| 181 | Ultra-high strength dual phase steels with excellent cryogenic temperature toughness | US099152 | 1998-06-18 | US6066212A | 2000-05-23 | Jayoung Koo; Narasimha-Rao V. Bangaru |
| An ultra-high strength, weldable, low alloy, dual phase steel with excellent cryogenic temperature toughness in the base plate and in the heat affected zone (HAZ) when welded, having a tensile strength greater than 830 MPa (120 ksi) and a microstructure comprising a ferrite phase and a second phase of predominantly lath martensite and lower bainite, is prepared by heating a steel slab comprising iron and specified weight percentages of some or all of the additives carbon, manganese, nickel, nitrogen, copper, chromium, molybdenum, silicon, niobium, vanadium, titanium, aluminum, and boron; reducing the slab to form plate in one or more passes in a temperature range in which austenite recrystallizes; further reducing the plate in one or more passes in a temperature range below the austenite recrystallization temperature and above the Ar.sub.3 transformation temperature; finish rolling the plate between the Ar.sub.3 transformation temperature and the Ar.sub.1 transformation temperature; quenching the finish rolled plate to a suitable Quench Stop Temperature (QST); and stopping the quenching. | ||||||
| 182 | Method of cooling steel sections which are hot from rolling | US826302 | 1997-03-27 | US5830293A | 1998-11-03 | Meinert Meyer; Rainer Kohlmann |
| A method of cooling steel sections which are hot from rolling by means of shock-like cooling following the rolling process so as to form a martensitic surface layer, and by subsequently autogenously tempering this surface layer by means of core heat to obtain a tough-resistant structure with an austenitic remaining cross-section, wherein the method is used in connection with types of steel which, with uncontrolled cooling in air, would directly transform from the austenitic phase into martensite because of their alloying elements from the group Cr, Mn, Mo, Ni and other suitable elements. | ||||||
| 183 | Method of making cold formed high-strength steel parts | US275602 | 1994-07-15 | US5453139A | 1995-09-26 | Hugh M. Gallagher, Jr. |
| A method of making high-strength steel parts is disclosed by providing a blank of high-strength steel having a ferrite-pearlite microstructure and high-strength mechanical properties and cold forming the blank by upsetting, forging, or extrusion to provide a part having a desired geometric configuration while the mechanical strength of the part remains substantially the same or greater than the blank. | ||||||
| 184 | Method for producing abrasion-resistant steel having excellent surface property | US98609 | 1993-07-28 | US5393358A | 1995-02-28 | Nobuo Shikanai; Tetsuya Sanpei; Kazunori Yako; Kenji Hirabe; Yasunobu Kunisada |
| An abrasion-resistant steel having excellent surface property consists essentially of 0.1 to 0.45 wt. % C, 0.1 to 1 wt. % Si, 0.1 to 2 wt. % Mn, 0.04 wt. % or less P, 0.04 wt. % or less S, 0.1 to 1 wt. % Ti, 0.0015 to 0.01 wt. % N, and the balance being Fe and inevitable impurities, the steel including at least 400 TiC precipitates of 0.5 .mu.m or more in particle size per 1 mm.sup.2 and the steel having Ti* of 0.05 wt. % or more and less than 0.4 wt. % the Ti* being defined by the equations of Ti*=Ti(a)-[Ti], Ti(a)=Ti-{(48/14)N+(48/32)S}, log[Ti][C]=(-10580/T)+4.38, [Ti]=4.times.[C]+{Ti(a) -4.times.C}.A method for producing an abrasion-resistant steel having excellent surface property comprising the steps of: preparing a molten steel having the composition specified above; casting continuously the molten steel to produce slab, coarse particles of TiC being precipitated in the slab; hot-working the slab to produce a hot-rolled steel sheet at 1300.degree. C. or less; and quenching the hot-rolled steel sheet. | ||||||
| 185 | Device to position a device in a cylindrical cavity comprising perforation disposed along a regular network | US516257 | 1990-05-01 | US5073332A | 1991-12-17 | Jean-Pierre Wanhem; Benoit Guillo |
| So as to position a device, such as an eddy current probe support inside a cylindrical cavity with radial perforations opening into said cavity, a device (36) is proposed, said device including a pole (50) orientated parallel to the axis of the cavity. This pole may occupy different pre-established indexing positions in rotation and in translation inside the cavity by means of a mechanism (42, 44, 54, 58, 60). In each of these indexing positions, an active head (98), mounted at the extremity of the pole (50) by means of a pantograph (66) and a cladding arm (100), is able to move in a specific active zone on the lower wall of the cavity. To this effect, the active head is clad by the arm (100) and is equipped with autonomous thrustors controlling its movement. | ||||||
| 186 | Process for cooling heated material | US196941 | 1988-04-21 | US4944174A | 1990-07-31 | Peter Muller |
| A heating bath including molten metal is situated at an entry into a hot roll mill such that the metal stock entering the hot roll mill passes through the heating bath to acquire heat therefrom. A cooling bath including molten metal is situated at an exit from the hot roll mill such that the metal stock exiting from the hot roll mill passes through the cooling bath delivering heat thereto. The molten metal in each of the baths is caused to flow counter to the direction of passing of the metal stock therethrough to form within each bath a hotter fraction and a cooler fraction of the molten metal. The molten metal is circulated between the heating bath and the cooling bath so that a hottest fraction of the molten metal in the cooling bath is transferred to the heating bath and a coolest fraction of the molten metal in the heating bath is transferred to the cooling bath. | ||||||
| 187 | Method for pressurized water quenching of rolled steel products | US703643 | 1985-02-21 | US4592788A | 1986-06-03 | Franz Tamm; Bernhard Hoericke; Arnold Joachim |
| A method for pressurized water quenching of rolled steel products wherein the product is cooled so abruptly on its surface, at a quenching from a final rolling temperature of approximately 1000.degree. C. to an equilibrium temperature of above 500.degree. C., the temperature of the core immediately after the completion of the quenching is no more than only 30.degree. C. below the original final rolling temperature. The shorter cooling periods lead to a thinner martensitic layer, and a greater portion of the ferritic-perlitic core mass resulting in an increase in ductility with little change in strength. | ||||||
| 188 | Method for the production of improved railway rails by accelerated cooling in line with the production rolling mill | US405514 | 1982-08-05 | US4486248A | 1984-12-04 | Robert J. Ackert; Robert W. Witty; Peter A. Crozier |
| Railroad rails having improved wear resistance, are produced by controlled forced cooling from above the austenite transformation temperature, to produce rails having a fine pearlite metallurgical structure in the head portions of the rails. Apparatus comprising a series of cooling headers utilizing a liquid cooling medium, such as unheated (i.e. cold, or ambient temperature) water, alternating with a series of air zones, is preferably arranged in line with the production rolling mill, to receive hot rails as they emerge from the mill, without the necessity of intervening reheating. A roller type restraint system transports the rails through the cooling apparatus, while restraining them in the appropriate position. Each segment of the rail length is intermittently subjected to forced cooling by spray application of the liquid cooling medium, applied to the head portion, and the central portion of the base bottom, of the rail, with means being provided to prevent spray from impinging on the web and base tips of the rail. During the intervals between applications of forced cooling, heat soaks back from the web portion of the rail, the operating parameters of the system being so arranged that the temperature of the rail remains essentially above the martensite formation temperature. A computerized control system discontinues the application of forced cooling, at a predetermined stop temperature, also above the martensite formation temperature. The apparatus and method are capable of producing rails having the desired fine pearlite structure in the head portion, on a consistent basis, notwithstanding wide variations in temperature between different rails, and different segments of the same rail, as they emerge from a conventional production rolling mill. | ||||||
| 189 | Method for producing aluminum powder alloy products having improved strength properties | US417796 | 1982-09-13 | US4435213A | 1984-03-06 | Gregory J. Hildeman; John C. Kuli, Jr.; Leo A. Vivola |
| Aluminum alloy atomized or other powder is compacted and shaped into a useful article including heating the compact rapidly by induction heating techniques. Such rapid induction heating results in improved strength or toughness properties without substantial penalty in elongation, thereby rendering the product so produced more useful in high strength applications. The product so produced may be subsequently shaped by forging, extruding or rolling processes. | ||||||
| 190 | Process for direct heat treatment of track links for tractors or tracked vehicles | US388715 | 1982-06-15 | US4419152A | 1983-12-06 | Walter Grilli; Franco De Meo; Ivan Franchini |
| Process for the manufacture of steel track links for tracked vehicles, comprising forging steel track links at an initial forging temperature of 1150.degree.-1200.degree. C. for 45-60 seconds with a finish forging temperature of 950.degree.-1050.degree. C., subjecting the links thus-produced to initial cooling at a rate of 2.degree.-4.degree. C./s to a temperature of 720.degree.-830.degree. C., maintaining the links at a temperature of 800.degree.-850.degree. C. for 2-3 minutes, again cooling the links at a rate of 10.degree.-15.degree. C./s to a second temperature of 180.degree.-380.degree. C., and maintaining the links at this second temperature for a period of 10-20 minutes, the steel having the following weight percent compositions:C: 0.30-0.38Mn: 1.00-1.50Cr: up to 0.60Si: 0.15-0.35S+P: about 0.06balance essentially iron. | ||||||
| 191 | Method of manufacturing rolled steel products with high elastic limit | US124794 | 1980-02-26 | US4295902A | 1981-10-20 | Marios Economopoulos |
| A rolled steel product is given an elastic limit of 500 to 1200 MPa by selection of a particular steel composition and a particular heat treatment. The steel contains 0.10-0.50% C, 0.90-1.50% Mn, and 0.10-0.45% Si, and optionally 0.20-0.70% Ni, 0.10-0.80% Cr, and 0.02-0.10% V. The heat treatment consists of surface quenching from above the austenitization temperature by means of a fluid, the heat remaining in the product being sufficient to temper the martensite and/or bainite in the quenched surface. | ||||||
| 192 | Heat-treated zirconium alloy product | US914829 | 1978-06-12 | US4226647A | 1980-10-07 | Erland M. Schulson; Donald J. Cameron |
| High tensile strength, creep and corrosion resistant zirconium alloys containing 7.0-10.0 wt % aluminum, 0-3 wt % in total of one or more elements selected from the group consisting of magnesium, tin, chromium, iron, carbon, silicon, yttrium, niobium, molybdenum and beryllium, the balance zirconium and incidental impurities, are produced by annealing cast alloys at a temperature below about 992.degree. C. for a period of time sufficient to produce alloys having a substantially continuous matrix of the ordered intermetallic compound Zr.sub.3 Al. The alloys may initially be hot worked at temperatures about 1000.degree. C., while in the .beta.Zr-Zr.sub.2 Al two phase region, prior to annealing. Preferred alloys contain 7.5-9.5 wt % aluminum, the balance zirconium and incidental impurities. | ||||||
| 193 | Heat-treating tubular steel sections | US950985 | 1978-10-13 | US4204892A | 1980-05-27 | Marios Economopoulos |
| A tubular steel section at a temperature, above Ac.sub.1, at which the steel contains at most 15% ferrite is subjected to martensitic and/or bainitic quenching followed by still air cooling. The effects of quenching are limited to a surface layer, internal and/or external, of the section. At the end of the quenching step the part of the section remote from the quenched surface layer or layers is at a temperature above 675.degree. C. which permits self-tempering of the quenched surface layer or layers at a temperature above 450.degree. C. and ensures transformation of residual austenite to a martensite-free structure. | ||||||
| 194 | Method of producing steel sections of improved quality | US904901 | 1978-05-11 | US4175985A | 1979-11-27 | Emile Blondelot; Marios Economopoulos; Stephan H. Wilmotte |
| A steel section 6 to 40 mm thick, emerging from a hot rolling mill at 1000.degree. to 800.degree. C. is surface quenched for 2 to 6 seconds at a cooling rate of the order of 1.5 to 5 MW/m.sup.2. During subsequent self-tempering of the quenched surface by heat from the remainder, the section tends to an equalization temperature of 500.degree. to 700.degree. C. | ||||||
| 195 | Hot bar cooling | US868056 | 1978-01-09 | US4146411A | 1979-03-27 | Ronald F. Dewsnap; David E. Beard |
| A steel rod or bar comprises an outer surface layer of ferrite-pearlite type structure, an annulus immediately below said surface layer having an acicular micro-structure comprising martensite and/or bainite and a core of bainite or martensite or ferrite and carbides or a combination of two or more of these constituents. | ||||||
| 196 | Brake disc and process for producing the same | US832777 | 1977-09-13 | US4126492A | 1978-11-21 | Hiromu Okunishi; Hideki Nakaji; Hiroyuki Suwa; Hideaki Sato |
| A brake disk and process for producing the same which is particularly suitable for use on motorcycles. A stainless steel material of particular chromium content is subjected to a heat-treating and press-quenching step to form a brake disk having a sufficient hardness required for the function of a brake and being of favorable appearance for use on motorcycles. | ||||||
| 197 | Rolled steel rod or bar | US617156 | 1975-09-26 | US4016015A | 1977-04-05 | Yves Jean Respen; Paul Andre Cosse; Mario Economopoulos |
| Steel rod or bar at the exit of the finishing stand of a hot rolling mill is superficially quenched, so that the surface layer of the rod or bar is given a bainitic or martensitic structure. Immediately after quenching, the core of the rod or bar is at about 850.degree. C and, therefore, still austenitic. Subsequent air cooling allows the austenite to transform to ferrite and carbides, while the surface layer is tempered by the heat transferred to it from the core. | ||||||
| 198 | In-line heat treatment of hot-rolled rod | US534001 | 1974-12-18 | US3939015A | 1976-02-17 | Raymond A. Grange |
| Hot rolled steel rod, containing less than 0.4% C, is cooled by a prescribed, interrupted-cooling procedure for producing rod with enhanced ability to receive cold work. In cooling from the austenite range, the rod is held within a specified, narrow temperature range for a period of at least about 2 minutes. The particular holding range is shown to be a function of carbon content, whereby low carbon steels (<0.28% C) are held at a prescribed temperature above 1,450.degree.F, while medium carbon steels are held at a temperature of about 1,250.degree.F. | ||||||
| 199 | Method for the production of high strength notch tough steel | US35942373 | 1973-05-11 | US3897279A | 1975-07-29 | SHAUGHNESSY REGINALD N; WITTY ROBERT W; ACKERT ROBERT J |
| A fully killed steel having a high yield strength and high notch toughness below 0*F. and containing by weight up to 0.20 percent carbon, at least 0.015 percent columbium and at least 0.75 percent manganese, said steel having a substantially uniform, fine grain, essentially ferritic grain structure with an average grain size of finer than 9.0 as determined by ASTM Test No. E 112, said steel preferably having a longitudinal Charpy Impact of at least 60, as well as a method of producing said steel which essentially involves continuously rolling the steel in the temperature interval 1700* to 1900*F.
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| 200 | As-worked bainitic ferrous alloy and method | US31696272 | 1972-12-20 | US3806378A | 1974-04-23 | BRAMFITT B; MARDER A |
| THIS INVENTION RELATES TO AN AS-WORKED BIANITIC FERROUS ALLOY AND TO A NOVEL METHOD OF PROCESSING SAME TO OBTAIN OPTIMUM STRENGTH AND TOUGHNESS. MORE PARTICULARLY, THIS INVENTION IS DIRECTED TO THE HOT WORKING CYCLE OF A FERROUS ALLOY CHARACTERIZED BY AN I-T DIAGRAM OR S CURVE HAVING A DOUBLE NOSE OR A PEARLITE TRANSFORMATION KNEE OF THE BEGINNING CURVE ABOVE A BROAD BIANITIC BAY REGION. SUCH AN ALLOY IS HEATED TO AN AUSTENITIZING TEMPERATURE OF ABOUT 1500* TO 2200*F., AND SUBJECTED TO A PLURALITY OF WORKING OPERATIONS AT SUCCESSIVELY LOWER TEMPERATURES, WHERE THE FINAL WORKING OPERATION IS CONDUCTED AFTER THE BEGINNING OF THE AUSTENITE TRANSFORMATION TO BAINITE AND BEFORE THE COMPLETE TRANSFORMATION THEREOF.
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