AU663997B2

AU663997B2 - Abrasion-resistant steel

Info

Publication number: AU663997B2
Application number: AU66065/94A
Authority: AU
Inventors: Yasunobu Kunisada; Masayoshi Kurihara; Nobuo Shikanai; Yukio Shironouchi; Saburo Tani
Original assignee: NKK Corp; Nippon Kokan Ltd
Current assignee: JFE Engineering Corp
Priority date: 1992-02-27
Filing date: 1994-06-29
Publication date: 1995-10-26
Anticipated expiration: 2012-03-10
Also published as: NZ241930A; FI921390A0; EP0557634A1; KR930018046A; FI921390A; KR950005927B1; CA2063327A1; AU1215592A; AU6606594A; ZA921683B; BR9201120A; JPH05239591A

Description

AUSTRALIA

Patvnto Act 1990 COMPLETE SPECIFICATION STANDARD PATENT Applicant: NKK CORPORATION Invention Title: ABRASION-RESISTANT STEEL

C

C C I 11 The following statement is a full description of this invention, including the best method of performing it known to US:

I

ABRASION-RESISTANT STEEL Title of the Invention Background of the Invention The'present invention.relates to an abrasion resistant steel used in the fields of construction, -civil engineering and mining such as in power, shovel, bulldozer, hopper and bucket.

Description of the Related Art Abrasion resistant steels are used in the fields of construction, civil engineering and mining such as in power shovel, bulldozer, hopper and bucket to keep the service lives of these machines or their parts. Since abrasion resistance of steel is increased by increasing hardness of steel, steel having a high hardness manufactured by applying heat treatments such as.quenching and the like to an alloyed steel has previously been used.

.r Methods for manufacturing an abrasion-resistant steel with high hardness are disclosed in Japanese Patent Application Laid Open No.142726/87, No.169359/88 and No.142023/89. It is an S'i object of those methods to obtain an abrasion-resistant steel I I by determining the Brinell Hardness of steel at about 300 or more and improving weldability, toughness and workability in bending. That is, the abrasion resistance of steel is obtained by attaining a high hardness of steel.

In recent, years, however, the properties required for abrasion-resistant steel have become severer and the essential solution to a higher abrasion resistance of steel will not be obtained by simply increasing the hardness of steel. When the hardness of steel is greatly increased on the basis of the conventinal technology, weldability and workability of steel deteriorate, and the production cost greatly increases due to a high alloying. Accordingly, it is easily anticipated that it is difficult in practical use to greatly increase the hardness of steel for the purpose of increasing the abrasion resistance of commercial steel.

The present invention is devised from a viewpoint quite different from the aforementioned idea on the production of abrasion-resistant steel, namely, the idea of increasing the abrasion resistance of steel by attaining a high hardness.

Summary of the Invention It is an object of the present invention to provide an abrasion-resistant steel obtained by increasing only the abrasion resistance of steel without greatly increasing the hardness of steel.

The present invention provides an abrasion-resistant steel consisting essentially of 0.05 to 0.45 wt.% C, 0.1 to 1 wt.% Si, L

UI'

-3- 0.1. to 2 wt. Mn, 0.2 to 1.5 wt. Ti and the balance being Fe and inevitable impurities, said steel including at least 200 of precipitates of 1.0 It m or more in average particle size per 1 mm 2 and said precipitates containing Ti.

The present invention provides another abrasion-resistant steel consisting of 0.05 to 0.45 wt. C, 0.1 to 1 wt. Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt Ti, at least one element selected from the group consisting of 0.1 to 2 wt. Cu, 0.1 to 10 wt.

Ni, 0.1 to 3 wt. Cr, 0.1 to 3 wt. Mo and 0.0003 to 0.01 wt. B and the balance being Fe and inevitable impurities, said steel including per square millimeter of cross section at least 200 of precipitates having an average particle size of greater 10 than or equal to tt m and said precipitates containing Ti.

The present invention provides still another abrasion-resistant steel consisting of 0.05 to 0.45 wt. C, 0.1 to 1 wt. Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt. Ti, at least one element selected from the group consisting of 0.005 to 1 wt. Nb and 0.01 to 1 wt. V and the balance being Fe and inevitable impurities, said steel including per square millimeter of cross section at least 200 of precipitates having an average particle size of greater than or equal to 1 p m and said precipitates -:.ntaining Ti.

The present invention provides yet another abrasion-resistant steel consisting of 0.05 to 0.45 wt. C, 0.1 to 1 wt. Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt. Ti, at least one element selected from the group consisting of 0.1 to 2 wt. Cu, 0.1 to wt. Ni, 0.1 to 3 wt. Cr, 0.1 to 3 wt. Mo and 0.0003 to 0.01 wt. B, at least one element selected from the group consisting of 0.005 to 1 wt. Nb and 0.01 to 1 wt. V and the balance being Fe and inevitable impurities, said steel Iincluding per square millimeter of cross section, at least 200 of precipitates having an average particle size of greater than or equal to 1 pL m and said precipitates Scontaining Ti.

DBII 117912 16 Augut 199 -4- In the context of the invention, the term average particle size is defined as the verage size of all of the particles determined by dividing the sum total of the particle sizes of each whole precipitate within an arbitrary cross section of steel by the number of whole precipitates. The particle size of the precipitate is obtained through observing the microstructure of the steel through an arbitrary cross-section.

The above objects and other objects and advantages of the present invention will become apparent from the following detailed description, taken in conjunction with the appended drawings.

S Brief Description of the Drawings Figure 1 is a graphical representation showing the relationship between the added amount of titanium and the number of precipitate of the present invention; r Figure 2 is a graphical representation showing the relationship between the number of coarse precipitates of 1.0 to 50 p. m in average particle size per 1 mm 2 and the abrasion resistance of the present invention; and Figure 3 is a giaphical representation showing in detail the range of 2000 of coarse precipitates or less per 1 mm 2 in Figure 2.

Description of the Preferred Embodiment The most significant feature of the present invention is to increase the abrasion resistance of steel by adding a great amount of titanium to steel and effectively utilizing hard coarse precipitates containing titanium. Accordingly, it is S B H:7912 16 AliSwl( 1995 n unnecessary in the present invention to enhance hardness of abrasion-resistant steel by only transforming the structure of steel to a martensite, which is the conventional way of enhancing the abrasion resistance of steel.

The conventional abrasion-resistant steel obtained by adding anium to the steel is known. In the conventional way, the purpose of addition of titanium to steel is mainly to fix nitrogen as TiN liable to combine with B in order to secure solution boron effective for quenching hardenability, and the added amount of Ti is about 0.02 wt.% or less. The addition of a large quantiy of titanium to steel has been generally limited due to the oxidation of titanium in the steel making stage, clogging of nozzles and reaction of titanium with an oxidation preventing powder in the casting stage. Therefore, the effect o the addition of a large quantity of titanium to steel has been not yet known.

When attempts are made to produce the effect precipitation hardening) of an increase of the strength of steel by using TiC, about 0.05 wt.% Ti is often added to steel. For the precipitation hardening, the particle size of a precipitate has been required to limit to 0.1 gm or less.

t, iThe inventors found after having conducted their detailed examination that the abrasion resistance of steel could be greatly increased by adding a great amount of titanium to steel and causing coarse precipitates of 1.0 m or more in average particle size consisting mainly of TIC or, TiN as precipitates, which do not contirbute to the precipitation hardening, to yl beenreqiredto imitto .1 un o les. precipitate and disperse in large quantities. The featur, f the present invention is not only to simply add a large qu"'Lty of titanium to steel, but also to utilize the coarse precipitates of 1.0 gm or more in average particle size, which have not been considered completely in a traditional common sense and moreover have been regarded as rather harmful. Since those coarse precipitates do not contribute to the precipitation hardening, the strength and hardness of steel are not increased. Accordingly, only the abrasion-resistance of steel of the present invention, which has a hardness equal to that of the prior art steel or smaller than that of the prior art steel, can be greatly increased.

The precipitates in steel of the present invention are composed of TiC, TiN and TiS. Precipitates of NbC and NbN are present in steel, to whic,; Nb is added. Precipitates of VC and VN are present in steel, to which V is added. Precipitates of Nb C, NbN, VC and VN are simultaneously present in steel, to which Nb and V are added. Precipitates containing Ti, Nb and V simultaneously are also present in the steel. As described above, in increasing the abrasion resistance of steel, the precipitates containing Ti are most effective. The precipitates containing Nb and V are also effective in an Sincrease of the abrasion resistance of steel.

p e The reason why the contents of elements of the invented steel are specified will now be descirbed as follows: C is an indispensable element in formation of the The precipitates containing Ti and has an effect of increase of the prsn nsel owii bi de. Peiiae fV n 6 hardness of steel. When a great amount of C is added to steel, the weldability and workability of steel are deteriorated.

Therefore, the upper limit of addition of C is determined at 0.45 The lower limit of addition of C is determined at 0.05 wt.% which is an amount necessary for realizing the effect of TiC as one of the precipitates containing Ti.

Si is an element effective in deoxidation process of steel making and a minimum addition of 0.1 wt.% Si is required for this purpose. Si is also an effective element for solution hardening. However, an addition of Si to steel over 1 wt.% lowers the toughness of steel and increases inclusions in steel.

In consequence, the content of Si in steel is limited to a range of from 0.1 to 1 wt.%.

Mn is an element effective in quenching hardenability of steel. From this point of view, at least 0.1 wt.% Mn is required for this purpose. However, when the Mn content exceeds 2 the weldability of steel is deteriorated.

Therefore, the Mn content is determined at 0.1 to 2 wt.%.

Ti is one of the most important elements as is C. The addition of at least 0.05 wt.% Ti is required to stably form a great amount of coarse precipitates containing Ti. The addition of 0.2 wt.% Ti or more is preferable to stably generate a greater amount of precip."ates containing Ti and to secure a better abrasion resistanw, of steel. Figure 1 is a graphical representation showing the relationship between the S added amount of Ti and the number of the precipitates containing Ti. When more than 1.5 wt.% Ti is added to steel, the steel -7- CP~xnl t b

I

"ii: possesses good abrasion resistance. However, a high cost is required for the production. The weldability and workability of steel lowered. The quenching hardenability of steel is also lowered. Therefore, the Ti content is required to be 0.05 to 1.5 wt.% and preferably 0.2 to 1.5 wt.%.

In addition to the above basic elements, if necessary, at least one element selected from the group consisting of Cu, Ni, Cr, Mo and B can be added to steel within the following range to enhance the quenching hardenability.

Cu is an element for enhancing the quenching hardenability of steel. However, when the Cu content is below 0.1 the effect is not sufficient. When the Cu content exceeds 2 wt.%, the hot workability of steel is lowered and the production cost is increased. Therefore, the Cu content is determined at 0.1 to 2 Moreover, to prevent the production cost from increasing and to secure the effect of addition of Cu to steel, the Cu content is desired to be in the range of 0.2 to 1.0 wt.%.

Ni is an element which enhances the qul-'ching hardenability of steel. When the Ni content is below 0.1 the effect is not sufficient. When the Ni content exceeds 10 the production cost is greatly increased. Therefore, the Ni content is determined at 0.1 to 10 Ni also is effective in increase of the low-temperature toughness. To prevent the production cost ifom increasing and to secure the effect of addition of Ni to steel, the Ni content is desired to be from 0.2 to 1.5 wt.%.

Cr is an element which enhances the quenching hardenabiltiy

I

i ii i i r i s i i 1:1 -8of steel. When the Cr content is below 0.1 the effect is not sufficient. When the Cr content exceeds 3 the weldability of stee is deteriorated and the production cost is increased. Therefore, the Cr content is determined at 0.1 to 3 To prevent the production cost from increasing and to secure the effect of addition of Cr to steel, the Cr content is desired to be from 0.2 to 1.5 wt.%.

Mo is an element which enhances the quenching hardenabiltiy of steel. When the Mo content is below 0.1 the effect is not sufficient. When the Mo content exceeds 3.0 the weldability of steel is deteriorated and the production cost is increased. Therefore, the Mo content is determined at 0.1 to 3 The Mo content is desired to be from 0.1 to 1 wt.% in terms of the production cost.

B is an element whose quenching hardenability is enchanced by adding a very small amount of B to steel. When the B content is below 0.0003 the effect is not sufficient.

When the B content exceeds 0.01 the weldability of steel is deteriorated and simultaneously the quenching hardenability 4 of steel is lowered. Therefore, the B content is determined at 0.0003 to 0.01 To prevent the production cost from increasing and to secure the effect of addition of B to steel, the B content is desired to be from 0.0005 to 0.005 wt.%.

To increase the precipitation hardening in steel in the present invention, at least one element selected from the group S. consisting of Nb and V can be added to steel within the following range: I 91 *6I 4 5* a

M

a.

(0- Nb is an element effective in the precipitation hardening of steel and can control the hardi;ess of steel according to the use of steel. When the Nb content is below 0.005 the effect is not sufficient. Nb is also effective in forming coarse precipitates as is Ti. When the Nb cortent is over 1 the weldability of steel is deteriorated. Therefore, the Nb content is required to be from 0.005 to 1 To prevent the production cost from increasing and to secure the effect of addition of Nb to steel, the Nb content is desired to be from 0.01 to 0.5 wt.%.

V is an element effective in the precipitation hardening and can control the hardness of steel according to the use of steel. When the V content is below 0.01 the effect is not sufficient. V is also effective in formation of coarse precipitates as is Ti. However, when the V content exceeds 1 the weldability of steel is deteriorated. Therefore, the V content is required to be from 0.01 to 1 To prevent the production cost from increasing and to secure the effect of addition of V to steel, the V content is desired to be from 0.03 to 0.5 wt.%.

The steel of the present invention is manufactured on condition that 200 or more of coarse precipitates of 1.0 u m in average particle size containing titanium are present per 1 mm 2 The abrasion resistance of steel as the most important feature of steel of the present invention can be obtained by causing the coarse precipitates containing Ti to be present in O Nb isa lmn fetv nth rcptto adnn of stee -n 1a coro th adeso telacrigt ,antAttorney for and onibehalf of the Applicant large quantities in the steel. When the precipitates have a small average particle size of less than 1 r m, the effect of increasse of the abrasion resistancce is small. Moreover, since the precipitates having such a small particle size is accompanied by the increase of the hardness and strength of steel due to the precipitation hardening, the object of the present invention cannot be attained. Accordingly, the object of the composition of the present invention is the coarse precipitates of 1. m or more in average particle size.

However, even in the case where the precipitates of lu m or more in average particle size are present in steel, when the number of precipitates per 1 mm 2 is less than 200, there is little effect of increase of the abrasion resistance of steel.

e It is understood that a great amount of precipitates numbering 200 /mm 2 or more are required to obtain the effect of increase of a good abrasion resistance of steel. Accordingly, the steel of the present invention can be manufactured on condition that 200 or more of coarse precipitates of l.Oum in average I particle size containing titanium are present per 1 mm 2 500 or more of coarse precipitates containing Ti per 1 mm 2 are desired to obtain a better abrasion resistance of steel.

Figures 2 and 3 are graphical representation showing the relationship between the amount the number of the precipitates per 1 mm 2 of the coarse precipitates containing Ti and the j abrasion resistance of steel the abrasion resistance ratio the magnification of the abrasion resistance of the objective steel when the abrasion resistance of a soft steel is LJ

II

t I t' ;1 determined at 1 According to this graphical representation, it is clearly seen that when the number of the precipitates is 200 /mm 2 or more, a good abrasion resistance of steel can be obtained and that when the number of the precipitates is 500 /mm 2 or more, a better abrasion resistance of steel can be obtained.

However, since the coarse precipitates containing Ti of more than 50u m in average particle size are liable to drop out, the efi',?Jt of increase of the abrasion resistance cannot be expected. Besides this, since the toughness of steel is 4 greatly decreased when such extremely coarse precipitates are present in steel in large quantities, it is better that the coarse precipitates containing Ti of more than 50 u m in average particle size are not present in steel. Accordingly, it is desirable that 200 or more of precipitates of 50 ii m or less in Faverage particle size are present per 1 mm 2 In the present invention, if 200 or more of precipitates of Lu m in average particle size per 1 mm 2 preferably 500 or more I of precipitates, are present, the predetermined abrasion resistance can be obtained. So long as the condition as mentioned above is satisfied, it is no trouble that precipitates other than precipitates including titanium are present or precipitates of less than le m containing Ti are present.

Since a desired abrasion resistance of steel of the present invention can be obtained by only specifying the composition of cI ,oo, the steel and the precipitation containing Ti, it is not necessary to specify the working condition and heat treatment I 2 optionally and even when those heat treatments of the steel are carried out, the feature of the steel of the present invention cannot be impaired.

To generate the aforementioned coarse precipitations of u m or more in particle size, it is necessary to control a solidification rate of steel during casting of the steel. The solidification rate is required to be 102 ["C/min or less.

When the solidification rate exceeds 102 /min 1, the solidification rate is extremely great. Even if an amount of Ti satisfying the conditions of the present invention is added to steel, the precipites become fine as a whole and it becomes difficult to generate 200/mm 2 of precipitates of 1 I m or more in average particle size, which should be the condition of the Spresent invention. However, since the solidification rate of I less than 1/102 °C/min] is too slow, the aforementioned extremely coarse precipitates of more than 50 u m are liable to be generated. Accordingly, the solidification rate is desired to be 1/102 "/min or more.

Steel of the present invention is desired to have hardness of 550 or less as a hardness level of steel for practical use.

Example The chemical compositions of samples are shown in Tables 1 I f to 3. Samples of from A to Z and from to are inade of steel of the present invention. Samples of from to 4re -13- 1 3 s1 n..m.r..fm \nn mmn,, n7nrl flftl*? made of the steel for comparison. The comparison steels D and 0 are steels whose Ti content is beyond the range of the present invention. The steels® and for comparison are steels whose C content is beyond the range of the present invention the Ti content is within the range of the present invention The process of making steels 15 mm in thickness manufactured by using each of the samples, the abrasion resistance ratio, the hardness HB the Brinell Hardness on the 1 1 1 1 1 1 1 a 14

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I. U I *i USo c surface of the samples and the amount of precipitates the number of precipitates of from 1.0 to 50 u m in average particle size per 1 mm 2 are shown in Tables 4.to 6.

The abrasion resistance ratio is a ratio estimated by a change of weight of steel in an abrasion resistance test. In this test, when the abrasion resistance of soft steel is determined at 1.0, the magnification of the abrasion resistance of a sample is represented as an abrasion resistance of the sample. The abrasion resistance of the sample is represented with the foumula: abraded weight of the soft steel/ abraded weight of the sample Accordingly, the greater the abrasion resistance ratio of steel, the better the abrasion resistance of steel. Silica sand containing 100% SiOz was used as abrasives.

The processes in the Tables are classified as follows: AR: as rolled; RQ: as quenched after heated to 900 °c following the rolling and air-cooling; -14- RQT: as tempered at the temperature shown in the parenthesis after RQ treatment; DQ: as directly quenched after finish rolled at 880 "C following the heating of the slab at 1150*C DQT: as tempered at the temperature shown in the parenthesis following DQ; and QT: as tempered at the temperature shown in the parenthesis following Q.

The steel for comparison (D corresponds to the steel A, B-I and D of the present invention and the Ti conter. is below the lower limit specified by the present invention. The number of precipitates of 1.0 g m or more in particle size also is below the lower limit specified by the present invention. The abrasion resistance ratio of the steel for comparisonO is 4.9.

On the other hand, the abrasion resistance ratio of steel A of the present invention is 6.5. The abrasion resistance ratio of steel B-I is 8.3. The abrasion resistance ratio of steel D o is 9.3. Although the abrasion resistances of the steels of the present invention are various depending on the Ti contents and the number of the coarse precipitates, the abrasion resistance of the steel D of the present invention is increased about twice V o as many as that of the steel for comparison The hardness of the steel of the present invention is rather lower than that of the steel for comparison D. Therefore, it is clearly seen that the object of the present invention, which is to increase only the abrasion resistance of steel without enhancing the hardness of the steel, is attained.

£I 1 5 Similarly, the steel for comparison corresponds to the steel L and N of the present invention. It is clearly seen that the abrasion resistance superior to that of the steel for comparison can be obtained in any of the steel of the present invention. The steel for comparison corresponds to the steel B-l. Although the Ti content satisfies the conditions of the present invention, the mumber of the coarse precipitates of u m or more in particle size is below the lower limit specified by the-present invention since the C content is below the lower limit specified by the present invention. Therefore, it is clearly seen that the abrasion resistance of the steel for comparison is greatly inferior to that of the steel of the present invention. In the steel for comparison the contents of alloying elements other than C and the number of the coarse precipitates are beyond thie range of the present invention and only the C content is higher than the upper limit i specified by the present invention. Although the abrasion resistance of the steel for comparison is good, the steel j has a very high hardness of 616. In consequence, the workability and .weldability of the steel is greatly inferior to those of the steel of the present invention. The steel for comparison cannot be put to parctical use.

As described above, steel of the present invention has a i good abrasion resistance, having the hardness equal to or below that of the conventional steel. The steel of the present invention is a good abrasion-resistant steel having a good abrasion resistance, workability and weldability, which has I I 1 -1 6u i At/ BCJH:n17912 16 Augut 1995 been ever seen. Therefore, it becomes possible to greatly increase the service lives of spare parts of machines which have been greatly abraded and have had a short service lives, and the spare parts which requre complicated working and an abrasion resistance can be easily manufactured.

t' 7 ji i-I 7 I A A~AA4~C~ rsznzrzzzc.~~4.

'a nfl fin, 'a L~U ~YAAJ~ .JUh~!U ~IN.

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Table1

[C

E

F

G

H

13

K

0 0. 29 0.29 0.28.- 0.31 0.-19 0. 14 0. 32 0. 34 0. 3 1 Chem ical. Compos it ion, r r a SiI Mfn C u N-i C r M Mo jN~b V N Cwt.% B and N in ppm 0 38 i 1 4. 4 0.70 0.09 0.37 0.

0.38 4 -4 4 0.73 38 I 0.37 Present.

Invent ion Present Invention Present Invention 1-4441 0. 7! 0.71 T t I 1' 4 1.41 Present Invention Present 0.33 0. 73 1.02 0.23 1. 1.08 32Prsn _____Invention 0.33 1.44 .77 jPresent G 02 0.5 9 22 lInvention 0.*34 0.-3 4 0. 26 0.38..

1.40 0. 0.25 0.4 24 Present f 4- 4 4. J 0. 72.

0.045 0. 41 Present I *1 1 4 4 1 J 0.71 0.3q 0.55 0.028 0-.041 0:*54 Present r .1 1.1~ ____Invention

J

0.99. 0. 23 0 2-2' 0-.044 o0.0 8 z Present Invention L 0. 2 9 0.

S S r1 i -4 0.70'1 11 J.j9[023 I 0. 044 9 0.0 8 23 Present 23 Invention

I

S..

555w ~0- 55

S

I

A Table 2 C JIMn[ Chemical Composition* B and N in ppm )I.

0- u N i Co M.o N b .V T i N

M

.0

P

Q

S

TF

U

0.

1 3 0 Present 1 3 0 0 .386 0:7 1 0.25 05 5 0.-2 3 0.045 0.19 *8 30 Invention, 3- .1 1. 02 0. 23 0. 045 0. 38 8 :31 Preentio 31 *0.3 11 0. 71.. 6 0 3 0 41 8 3 Invention 0.3- 0380304 -18 3 Present 3_ 2_ 0 1 8 4 Invention Present 3*3 37 1.62 0.154 0. 98 4 Invention Present 33 0.28 '0 .2 2 0.88 0 .0.70 0. 44 15' 3 Invention .2 8 35 71 0.95 L.26 *0 -4'53 '0.47 12 34' Present ___Invent ion: 3 0 E 37 70 OA 5 .0.24' 219 38 Invention 18- 0. 44 1. 52 38 78 418' .0 .3 .3 rsn 6050 0.8 1 *r r. r -n

:I

II

Table 3 Chkmicaf Composi.tion wt.%, B and N in ppm I r S i Mn Cu N i Q r M o Nb 4. .1

V

x

Y

yZ 31.

0.42 0 27 j0.3Z 0.58 i.22 0.212 .347 a. is Present Invention 0.720.0.289 1 37110 26 Present L-ILL I I-026 Invent ion 0. 2 1.02 27 I.02 0 .4 72 0.32 Present Invention

I

0.

33.

I I 0.73 0.32 0. 251 0.41 Present Inven t ion! 4 1 4. 4.

41l 0.82 0.29 0. 583 0.48 Present Invention z .8 OA ,5 1. 18 -1.7 .39Present a ~1.77 .0.39 *11 128 Peet.

1.J Invention" SS0.3510.12- 0.96 0.41. 1.58 0.12 0.58 52. Present _Invention 44~ 04 Preseit' 0. 400. .7 71.33 J.89 0.45.- 1o4 0 Invent'o (D 0.30j0.3 0 0. 75_ 002 37 Comparison 0.30 .0.30 0.95 .1.03 0.21 0.045 0.1 .*11 47 Comparisor 0-.03 0 30 0.750- 0.47 37 Comparison 1I 0.5S/.3 1..50 0.31 Comparison I. 1 4. 4.

g ;j I- rCIL ;Pn~ C- C- 0 00 0 0 00 00 00 0 Table 4 Manufacturing Prc A RQ-- .RQ'7 B8- 2. Ra-T(4 0 0C.) 0-2 DQ0T (400-C) D0-

Q,

Abras ion Res istance Ratio 6.5 8.

Hardness

(HB)

Amount of Precipitates *of 1.0 Unm number/mmn 2 2 4 1' 474 Inveniion T

I

3 9.3 9 3.2 Invention 4 6.'l 27 7.

.90 1 Invention.

t 4- f 4 .9.7 33 5. 3 01 1 Invention 6. 8 .245 2 9.8 9 Invent ion 9. 3 242 4 1 90 Inventionl 8. 6 3*90 1 113*2 Inventior"k '1 -34 32 1 3-2 5 5 Inventiofli 4.7 3 02 1 2 08 Inventiori 3. 4 2-5 3 5 3 Invention 1 45 1 1 1 18 5 Invention 8. 9 1 7 1 5.6 0 Invention- 6 4 5 03--- 2 3 6 Invent i on 2 3 6.

I 1 1. n 11 1 S 2 5.3 8.2 5 0 7' 2-6 6 Invention-.

Inventioni 8.2 Z 6 6 Table t~3

I

Manufactu- Abrasion Hardness Peiiae ring Resistance (HB) Preipiate {Process I Rat io of1 0 U u mm 2 M A R 4.7 2 86 7 799 Invention 2 R Q. 4 9. 1 4 54 7 67. 1Inverft ion! N -1 A R 6. 1 *27 4 9 98 Invention N-2 R Q 6 4 48 9 63 .Invention.

A- AR. 7.3 2 46 3 76 0 Invention R Q 1.1 .2.7 5 3 658 Invention -P1 R Q 1 2-.8 4 6 1 1.2 1.0 Invention P-2 'FA R 9. 0 2 71 1 3 07 Invention o- R.Q 1 3. 1 .2 7 8 3 2 1 1 Inverition.

Q -z2 Q T(500.C) j 6. 4 25S'S 3. 18-6. .Invention 4R D Q 1 3.i 48 .1 3 89 .Inven tion .S-1 D Q 13.0 .4 09 18-77-- Inventioni S-21 D QT (550*O) 7 6- 2'97'7 2 18'9 Invention Tj R Q: 1 1.9 2-5--3 4 0 35 ~Invention U R> RQ. 8. 6 2 62 9 87 jInvention 4-il t7 *0 4 4 .4 Table 6

P

V.

Yj' ZjT anufactu ing rocess R Qr I- Abrasion Resistance Rati o Hardness

(HB)

Amount of Precipitates of 1.0 IL M (nurnber/nrn) I I~ 8. 7 43 2 62 3 Invention.

R Q .10.2 454 1 631. Inventionl R Q 9. 2 40-1 9 0 3 Invention R Q. 94 471 .1 19 7 Invention

CO,

R Q 9. 4. 4 29 1 4 8 2 Invention a' R Q 8- 3 80 9 50 tInvention]

C

R Q.

R Q R Q 5 40 4 1 38 9 Invention -r 4.

1 1.3 4 6 1.

1 61 5 Invention 4.Invention 4. 9 46 4 5 2 'Crrnrar isol AR:: 2.8- :326 3f .compar isol R Q 2 4 81 0_ R.Q R Q 1.

I..

4 1 1 18 Cornparisor 1. 2 1 22 501 I 4- 3. 1 6 1 6 1 5 2 9 Comparis.011 3.1 616. 1529 rCornpatiS.O~

Claims

1. An abrasion -resistant steel consisting of 0.05 to 0.45 wt. C, 0.1 i to 1 wt. Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt. Ti and the balance being Fe and inevitable impurities, said steel including per square millimeter of cross section at i 5 least 200 of precipitates having an average particle size as hereinbefore defined of greater than or equal to 1 pt m and said precipitates containing Ti.

2. The abrasion resistant steel of claim 1, wherein said steel includes per square millimeter of cross section at least 500 of precipitates having an average particle size as hereinbefore described of greater then or equal to 1 pL m.

3. The abrasion resistant steel of claim 1, wherein said precipitates have an average particle size of from 1 to 50 p. m.

4. An abrasion-resistant steel consisting of 0.05 to 0.45 wt. C, 0.1 to 1 wt. Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt. Ti, at least one element selected from the group consisting of 0.1 to 2 wt. Cu, 0.1 to 10 wt. Ni, 0.1 to 3 wt. Cr, i, 0.1 to 3 wt. Mo and 0.0003 to 0.01 wt. B and the balance being Fe and inevitable impurities, said steel including per square millimeter of cross section at least 200 of precipitates having an average particle size as hereinbefore described of greater than or equal to 1 p. m and said precipitates containing Ti. The abrasion resistant steel of claim 4, wherein Cu content is from 0.2 to 1 wt. Ni content is from 0.2 to 1.5 wt. Cr content is from 0.2 to 1.5 wt. Mo content is from 0.1 to 1 wt. and B content is from 0.0005 to 0.005 wt.

6. The abrasion resistant steel of either claim 4 or 5, wherein said steel includes per square millimeter of cross section, at least 500 of precipitates having an average particle size as hereinbefore described of greater than or equal to 1 pt m. r ii j~I precipitates have an average particle size of from 1 to 50 t. m. Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt. Ti, at least one element slIected from the group consisting of 0.005 to 1 wt. Nb and 0.01 to 1 wt. V and the balance being Fe and inevitable impurities, said steel including per square millimeter of cross section, at least 200 of precipitates having an average particle size as hereinbefore described of greater than or equal to 1 p m and said precipitates containing Ti.

9. The abrasion resistant steel of claim 8 wherein Nb content is from 0.01 to 0.5 wt. and V content is from 0.03 to 0.5 wt. The abrasion resistant steel of either of claim 8 or 9, wherein said steel includes per square millimeter of cross section at least 500 of precipitates having an average particle size of greater then or equal to 1 pm. S11. The abrasion resistant steel of any one of claims 8 to 10, wherein said precipitates have an average particle size of from 1 to 50 g m.

12. An abrasion-resistant steel consisting of 0.05 to 0.45 wt. C, 0.1 to 1 wt. Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt. Ti, at least one element selected from the group consisting of 0.1 to 2 wt. Cu, 0.1 to 10 wt. Ni, 0.1 to 3 wt. Cr, 0.1 to 3 wt. Mo and 0.0003 to 0.01 wt. B, at least one element selected from the group consisting of 0.005 to wt. Nb and 0.01 to 1 wt. V and the balance being Fe and inevitable impurities, said steel including per square millimeter of cross section at least 200 of precipitates having an average particle size as hereinbefore defined of greater than or equal to 1 pI m and said precipitates containing Ti. 2r

13. The abrasion resistant steel of claim 12, wherein said steel includes per square Si, 0.1 to 2 wt. Mn, 0.2 to 1.5 wt. Ti, at least one element selected from 9 26 millimeter of cross section at least 500 of precipitates having an average particle size of greater than or equal to 1 It m.

14. The abrasion resistant steel of either claim 1 or 12, wherein said precipitates have an average particle size of from 1 to 50 It m.

15. An abrasion resistant steel substantially as described in the examples of the present invention. DATED: 16 August 1995 CARTER SMITH BEADLE Patent Attorneys for the Applicant: NKK CORPORATION Sii *791 16 A *9 i ABSTRACT OF THE DISCLOSURE An abrasion-resistant steel consists essentially of 0.05 to 0.45 wt.% C, 0.1 to 1 wt.% Si, 0.1 to 2 wt.% Mn, 0.05 to wt.% Ti and the balance being Fe and inevitable impurities, the steel includes at least 200 of precipitates of 1.Ou m or more in particle size per 1 mm 2 and the precipitates contains Ti. In addition to the above basic elements, at least one element selected from the group consisting of 0.1 to 2 wt.% Cu, 0.1 to 10 wt.% Ni, 0.1 to 3 wt.% Cr, 0.1 to 3 wt.% Mo and 0.0003 to 0.01 wt.% B is added to steel or at least one element selected from the group consisting of 0.005 to 1 wt.% Nb and 0.01 to 1 wt.% V is added to steel. C C C C o 1 r i